WO2021038102A1 - Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique - Google Patents

Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique Download PDF

Info

Publication number
WO2021038102A1
WO2021038102A1 PCT/EP2020/074218 EP2020074218W WO2021038102A1 WO 2021038102 A1 WO2021038102 A1 WO 2021038102A1 EP 2020074218 W EP2020074218 W EP 2020074218W WO 2021038102 A1 WO2021038102 A1 WO 2021038102A1
Authority
WO
WIPO (PCT)
Prior art keywords
zinc
alloy coating
zinc alloy
phases
metal substrate
Prior art date
Application number
PCT/EP2020/074218
Other languages
English (en)
Inventor
Yutao Pei
Masoud Ahmadi
Original Assignee
Rijksuniversiteit Groningen
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Rijksuniversiteit Groningen filed Critical Rijksuniversiteit Groningen
Priority to KR1020227010436A priority Critical patent/KR20220054384A/ko
Priority to EP20764085.5A priority patent/EP4022102A1/fr
Publication of WO2021038102A1 publication Critical patent/WO2021038102A1/fr

Links

Classifications

    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • 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
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process

Definitions

  • the invention relates to a method for the characterisation of formability properties of a zinc alloy coating on a metal substrate and a metal substrate comprising a zinc alloy coating.
  • Zinc-coated steels produced via hot-dip galvanization (HDG) process are regarded as the vital materials for household, construction and automotive industries.
  • the resultant ZnAIMg coatings offer superior corrosion resistance and friction/wear performance.
  • these recent hot-dip ZnAIMg coatings currently deliver rather low cracking resistance once subjected to forming processes.
  • Microstructural damages of ZnAIMg coatings lead to cracking in severely deformed areas and result in the formation of large cracks and subsequently deteriorate the in- service corrosion resistance.
  • EP33698308 for example, a zinc alloy plated steel sheet with good bending workability was disclosed, having a microstructure of a ZnAIMg coating with greater than 50% of the primary zinc phases having a preferred zinc orientation [0001]
  • JP2010255084 the crack resistance was improved by adding 0.005 to 0.2% by weight of nickel to a metal coating further comprising 1 to 10% by weight of aluminum and 0.2 to 1% by magnesium weight to alter the microstructure of the alloy.
  • a method for the characterisation of formability properties of a zinc alloy coating on a metal substrate is provided.
  • the zinc alloy coating containing one or more alloying elements selected from the group consisting of Mg, Al, Ni each with a content of at least 0.3 weight % and at most 10 weight %, optionally one or more additional elements selected from the group consisting of Si, Sb, Pb, Ti, Ca, Mn, Sn, La, Ce, Cr, or Bi, wherein the content by weight of each additional element in the metallic coating is less than 0.3 weight %, inevitable impurities, the remainder being zinc,
  • the zinc alloy coating having a microstructure comprising a primary phase and a binary eutectic and/or ternary eutectic phase
  • Electron Backscatter Diffraction EBSD
  • n crystallographic orientation-dependent strain hardening exponent
  • the crystallographic orientation-dependent strain hardening exponent (n) may be determined for all phases of the microstructures, of, e.g. primary zinc phase, binary eutectic phase and ternary eutectic phase.
  • the crystallographic orientation-dependent strain hardening exponent (n) is at least determined for the primary zinc phase.
  • the tendency for cracking of the zinc alloy is related to the micro ductility of the coating.
  • the method according to the invention is a solution to reveal and analyse which microstructural phases are most detrimental for crack initiation.
  • the crystallographic orientation-dependent strain hardening exponent (n) can be obtained directly from EBSD or via a combination of EBSD and nanoindentation tests.
  • EBSD is well known in the field and related experimental settings are described in IS013067:2011.
  • the zinc alloy has a hexagonal close-packed crystal structure (HPC). This HPC packing of the zinc alloy allows to determine the strain hardening exponent (n) with respect to the crystal orientation from EBSD measurements, which surprisingly provided a good indication for cracking.
  • the binary eutectic phase exhibited on average lower strain hardening exponents then the primary zinc phase or ternary eutectic phase, which corresponds to the general observation that the binary eutectic phase is more prone to cracking.
  • the cracking tendency between primary zinc phase with different strain hardening exponents can also be derived from the method according to the invention.
  • the crystallographic orientation-dependent strain hardening exponent (n) provides a way to describe the cracking tendency for all phases in the zinc alloy coating of the metal substrate, and shows that a microstructure with a low n value has a higher likelihood to show cracking.
  • the method according to the invention may be used for a zinc alloy coating on any metal substrate, e.g. a metal or metal alloy, but in most cases will be a steel strip or a steel blank.
  • a metal substrate e.g. a metal or metal alloy
  • BH Bake Hardening
  • D&l Drawn and Wall Ironing
  • a Schmid factor (m) of the zinc alloy coating microstructure is determined.
  • the Schmid factor (m) may be determined for all phases of the microstructures, e.g. primary zinc phases, binary eutectic phase and ternary eutectic phase.
  • the Schmid factor (m) is at least determined for all primary zinc phase. It was found by the inventors that the Schmid factor gave an additional indication for the cracking tendency of the coating, especially when considering the primary zinc phase under strain conditions. It was found that the primary zinc phase with a high Schmid factor can bear the imposed deformation without cracking. Hence the Schmid factor provides an additional indication for the cracking tendency of zinc alloys on a metal substrate under strain.
  • the Schmid factor was determined from the EBSD analysis.
  • the Schmid factor (m) map of the areas was calculated.
  • the principle zinc slip systems including all the equivalent crystallographic families were considered and the corresponding Schmid maps were calculated and plotted according to tensile principle stress tensor along loading direction. By this process, the Schmid factor (m) of each cracked and non-cracked zinc phase was determined.
  • an orientation angle (Q) between the c-axis of hep crystal of the primary zinc phase and the loading direction is determined.
  • the orientation angle (Q) was found to be a factor important for the deformation mechanisms of the zinc alloy.
  • This orientation angle (Q) can be obtained from the inverse pole figure (IPF) orientation maps generated on the EBSD data as well known to a person skilled in the art. Accordingly, for each primary zinc phase, orientation angle (Q) between the c-axis of HCP zinc crystal and the loading direction was determined. It was found that the orientation of the basal plane of the primary zinc phase was preferably oriented parallel to the tensile load direction, to reduce cracking.
  • the strain hardening exponent (n) is determined with nanoindentation tests (ISO 14577-4:2016).
  • the crystallographic orientation-dependant strain hardening exponent (n) associated with each indent was calculated using EBSD and raw nanoindentation data by the method described by Dao et al, Computational modeling of the forward and reverse problems in instrumented sharp indentation, Acta Mater. 49 (2001) 3899-3918. doi: 10.1016/S1359-
  • n 1.428x10- 8 0 4 -2.233x 10- 6 0 3 + 1.027x1 O 4 0 2 -4.631 x 1 O 4 0+O.29, wherein Q is ranging from 0 - 90 °, as determined with EBSD as described above.
  • the strain hardening exponent (n) of the primary zinc phases can be determined from Q, which significantly simplifies the method according to the invention as Q, and hence n can be easily acquired from EBSD measurements alone.
  • the variables a,b,c,d and e are characteristic for the zinc alloy coating and can be empirically determined from an indented sample. For each indented primary zinc phase, the orientation angle (Q) between the c-axis of HCP zinc crystal and the loading direction (surface normal for nanoindentation) as determined by EBSD was plotted versus the corresponding local strain-hardening index (n) as determined by nanoindentation. The procedure was repeated for all the indented zinc phases.
  • a metal substrate comprising a zinc alloy coating, the zinc alloy coating containing one or more alloying elements selected from Mg, Al, Ni each with a content of at least 0.3 weight % and at most 10 weight %, optionally one or more additional elements selected from among Si, Sb, Pb, Ti, Ca, Mn, Sn, La, Ce, Cr, or Bi, wherein the content by weight of each additional element in the metallic coating is less than 0.3 weight %, inevitable impurities, the remainder being zinc, wherein the microstructure of the zinc alloy coating comprises primary zinc phases and a binary and/or ternary eutectic phase, wherein the primary zinc phases have a crystallographic orientation-dependant strain hardening exponent (n) of at least 0.29 as determined by the method as described above.
  • alloying elements selected from Mg, Al, Ni each with a content of at least 0.3 weight % and at most 10 weight %
  • additional elements selected from among Si, Sb, Pb, Ti, Ca, Mn, Sn, La, Ce
  • a metal substrate with a zinc alloy coating with a primary zinc phase with a higher n not only has a low tendency towards cracking, but may also rescue cracks initiated in other primary zinc phases or eutectic phases.
  • the primary zinc phases has a n of at least 0.29, preferably an n of at least 0.33, more preferably an n of at least 0.34, most preferably an n of at least 0.35.
  • a suitable upper limit for the n of the primary zinc phases is 1.00, as a primary zinc phase with a n above 1.00 would be unlikely to obtain according to standard production method.
  • the primary zinc phases of the zinc alloy coating has a Schmid factor m between 0.01 - 0.5, preferably between 0.33 - 0.5, more preferably between 0.34 - 0.5, most preferably between 0.35 - 0.5.
  • the cracking tendency of a primary zinc phase decreases with an increase in the Schmid factor.
  • At least 55% of the primary zinc phases of the zinc alloy coating have a Q > 45 °, preferably Q > 60 °, more preferably Q > 65 °, it was observed that primary zinc phases having a Q above 45° showed less cracking and were able to rescue initiated cracks in other phases.
  • the primary zinc phases preferably at least 55% have a Q > 45 °, preferably Q > 60 °, more preferably Q > 65 ° to ensure that the overall integrity of the zinc alloy coating is maintained, more preferably at least 65% of the primary zinc phases have a Q > 45 °, preferably Q > 60 °, more preferably Q > 65 °, most preferably at least 75% of the primary zinc phases have a Q > 45 °, preferably Q > 60 °, more preferably Q > 65 °.
  • the primary zinc phases of the zinc alloy coating have a crystallographic orientation-dependant strain hardening exponent n >0.33, preferably n>0.34, more preferably n>0.35. It was observed that primary zinc phases having n above 0.33 showed less cracking and were able to rescue initiated cracks in other phases. Without wishing to be bound by theory, it is believed that the different crystallographic orientation of primary zinc phases possess different magnitudes of local strain hardening exponent as a result of HCP mechanical anisotropy. Accordingly, if more than 75% of primary zinc phases in the zinc alloy have an unfavourable orientations with respect to loading direction, exhibiting n ⁇ 0.33, this will result in significant cracking during tensile/bending deformation;
  • the primary zinc phases preferably at least 75% have a n >0.33, preferably n>0.34, more preferably n>0.35 to ensure that the overall integrity of the zinc alloy coating is maintained, more preferably at least 80% of the primary zinc phases have a n >0.33, preferably n>0.34, more preferably n>0.35.
  • At least 55 % of the primary zinc phases have a Schmid factor m > 0.32, preferably m>0.33, more preferably m>0.35. It was observed that primary zinc phases having a m above 0.32 showed less cracking and were able to rescue initiated cracks in other phases.
  • the primary zinc phases preferably at least 55% have a m > 0.32, preferably m>0.33, more preferably m>0.35 to ensure that the overall integrity of the zinc alloy coating is maintained, more preferably at least 65% of the primary zinc phases have a m > 0.32, preferably m>0.33, more preferably m>0.35, most preferably at least 75% of the primary zinc phases have a m > 0.32, preferably m>0.33, more preferably m>0.35.
  • the primary zinc phases with a low Schmid factor (m ⁇ 0.32) lack a dislocation motion for plastic deformation, and therefore are more likely to experience cracking.
  • the zinc alloy coating comprises 5 to 35 % of a binary eutectic phase. It was also found by the inventors that most cracks initiated from the binary eutectic phase. The binary eutectic phase also showed a low n, on average below 0.10, showing a high tendency for cracking and a low tendency for rescuing cracks of neighbouring phases. Hence, the presence of binary eutectic phase is preferably maintained between 5 - 35%, more preferably between 5 - 20%, more preferably between 5 - 10%. In this range, initiated cracks in the binary eutectic phase can still be rescued sufficiently by the surrounding phases to maintain the overall integrity of the zinc alloy coating on the metal substrate.
  • the zinc alloy coating is free from binary eutectic phase. As most cracks initiate in the binary eutectic phase having a n well below 0.3, on average below 0.10, a zinc alloy coating free from binary eutectic phase is believed to have significantly less cracking.
  • the zinc alloy coating comprises 0.3 - 5 weight % Al and 0.3 - 5 weight % Mg, more preferably the zinc alloy coating comprises 1 - 2 weight % Al and 1-2 weight% Mg, as such a coating has improved corrosion resistance, stone chipping resistance as compared to conventional zinc coatings.
  • the zinc alloy coating is a hot dip coating.
  • the zinc alloy coating can be applied on the metal substrate in all common methods as known to a person skilled in the art
  • the metal substrate according to the invention preferably has preferably a zinc alloy coating made by hot-dip coating.
  • Hot-dip coating is well known to a person skilled in the art and has the advantage that it is a reliable and relatively cheap method to apply a zinc alloy coating to at least one side of the metal substrate.
  • the zinc alloy coating microstructure comprises phases with varying strain hardening exponents, wherein at least 70% of the phases with a crystallographic orientation-dependant strain hardening exponent n ⁇ 0.33 are surrounded by phases with a crystallographic orientation-dependant strain hardening exponent n > 0.33. It was found by the inventors that initiation of cracks in the alloy coating could either end up as a crack or could be rescued, leading to an overall acceptable coating layer. As elaborated already, the propagation of cracks involve phase boundaries. Hence, a crack could initiate in a phase with a low n, e.g. binary eutectic phase, and could propagate in a phase with a high n, e.g.
  • FIG. 1 Shows a schematic representation of microstructural cracking behaviour within ZnAIMg coatings.
  • FIG. 2 Shows Zn HCP crystal orientation with the loading parallel to the rolling direction (RD).
  • 2a shows Zn HCP crystal orientation favoured for cracking resistance, with a high m value (0.5)
  • 2b depicts Zn HCP crystal orientation favoured for cracking resistance, with a medium m value (0.32 - 0.45)
  • FIG 2 (c) shows Zn HCP crystal orientation leading to cracking.
  • FIG. 3 Depicts the EBSD results of a cracked area after 10% strain subjected to uniaxial tension, including image quality (IQ), IQ plus inverse pole figure (IPF), corresponding Schmid map and HCP crystals of the critical numbered phases.
  • IQ image quality
  • IPF IQ plus inverse pole figure
  • Schmid map HCP crystals of the critical numbered phases.
  • FIG. 4. Shows the principal zinc slip systems.
  • FIG. 5 Shows the n-value distribution for three samples (11, I2, C1) and their EBSD Image Quality Map
  • FIG. 1 Shows stage I of a cracking path that begun with a nucleation of tiny micro cracks in MgZn2 platelets of binary eutectic phase as the result of strain localization.
  • the binary eutectic phase has a low n of about 0.08 and is therefore prone to cracking.
  • stage (II) in FIG. 1
  • stage (II) in FIG. 1
  • the first circumstance is that the adjacent Zn phase exhibits an orientation close to [0001] perpendicular to the loading direction delivering Q > 60° and/or m > 0.32, in accordance to the claims.
  • the primary slip systems of Zn phase are activated by easy dislocation motion and subsequently ductile plastic deformation takes place instead of cleavage cracking (assuming the force direction is parallel to RD). Consequently, the crack is arrested in the primary zinc phase boundary.
  • the adjacent Zn phase possesses an orientation with HCP c-axis parallel to the loading direction (see Fig. 2c) and incorporates low m and n, serving as a favourable site for the propagating crack (e.g. cracked Zn phase No. 2 at stage III, Fig. 1).
  • FIG. 1 delivers the typical cracking mechanisms of ZnAIMg coatings; however, an individual crack may also form in a zinc phase with unfavorable orientation (m ⁇ 0.32) without prior nucleation in the binary eutectic phase.
  • the cracking behaviour of a zinc alloy coating can be easily measured and predicted by analysing n.
  • the other parameters, m and Q provide additional information to the cracking mechanism leading to a complete picture.
  • EBSD results were obtained according to the method according to the invention.
  • a metal substrate (HSLA grade steel) with a zinc alloy coating (Zn1.6AI1.6Mg) was prepared for nanoindentation and electron backscatter diffraction (EBSD).
  • EBSD electron backscatter diffraction
  • a square sample (1x1 cm) was cut from the coated metal sheets.
  • the surface of the zinc alloy coated samples was slightly mechanically polished using 1 pm diamond suspension and water-free lubricant on a Struers MD Nap disc for 3-5 minutes to obtain relatively smooth surface. Thereafter, the sample was flat ion milled for 15 minutes by means of an ion polisher (JEOL IB-19520CCP) in order to attain a good surface quality.
  • the in-situ SEM tensile and bending specimens were also prepared with the same procedure given above, before performing the tests.
  • Nanoindentation tests were conducted utilizing MTS Nano Indenter XP® with Berkovich tip using the continuous stiffness measurement (CSM) mode. Load controlled indentations with an applied force of 3 mN and spacing of 8 pm between the indents were performed on the coating microstructure.
  • CSM continuous stiffness measurement
  • EBSD measurements on the indented regions of the coating were conducted. For this, the sample was placed in a SEM chamber with 70° tilting angle. The region of interest was selected and a working distance of 12-15 pm was applied. A step size of 200 nm and accelerating voltage of 25 kV were used to acquire EBSD patterns. EBSD measurement was conducted on the cracked areas of specimens subjected to in-situ tensile and bending tests. The obtained EBSD results were analyzed by means of EDAX-TSL OIMTM Analysis 8 software. The image quality (IQ), inverse pole figure (IPF) orientation maps were generated on the EBSD data on the indented regions.
  • IQ image quality
  • IPF inverse pole figure
  • orientation angle (Q) between the c-axis of HCP zinc crystal and the loading direction (surface normal for nanoindentation) was determined and plotted versus the corresponding local strain-hardening exponent (n) of each labeled zinc phase which was achieved previously by nanoindentation.
  • the procedure was repeated for all the indented zinc phases.
  • a fourth order polynomial expression was fitted on the obtained cure to establish a relationship between Q and n.
  • FIG 4 shows the principle Zn slip systems including all the equivalent crystallographic families which were considered to calculate the corresponding Schmid maps, which was plotted according to tensile principle stress gradient along rolling direction (RD), as described also in R. Parisot, et al., Deformation and Damage Mechanisms of Zinc Coatings on Hot-Dip Galvanized Steel Sheets: Part I. Deformation Modes, Metall. Mater. Trans. A Phys. Metall. Mater. Sci. 35 A (2004) 797-811 and C. Tome et.al, The yield surface of hep crystals, Acta Metall. 33 (1985) 603-621.
  • RD tensile principle stress gradient along rolling direction
  • n 1.428xlO 8 0 4 -2.233xlO 6 0 3 + 1.027x10 4 0 2 -4.631xlO 4 0+O.29
  • Cracking quantification and fraction of phases were measured by image analysis It can been seen that the inventive samples 11 and I2, having at least 75% of primary phase crystals with an n > 0.33 leads to significantly less cracking, and shorter average crack length, than the sample C1 having less than 75% of the primary phase crystals with n > 0.33.

Landscapes

  • 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)
  • Other Surface Treatments For Metallic Materials (AREA)

Abstract

La présente invention concerne un procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique, et un substrat métallique comprenant un revêtement d'alliage de zinc. Dans le procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique, le revêtement d'alliage de zinc contient un ou plusieurs éléments d'alliage choisis dans le groupe constitué par Mg, Al, Ni ayant chacun une teneur d'au moins 0,3 % en poids et au plus 10 % en poids, éventuellement un ou plusieurs éléments supplémentaires choisis dans le groupe constitué par Si, Sb, Pb, Ti, Ca, Mn, Sn, La, Ce, Cr, ou Bi, la teneur en poids de chaque élément supplémentaire dans le revêtement métallique étant inférieure à 0,3 % en poids, des impuretés inévitables, le reste étant du zinc, le revêtement d'alliage de zinc ayant une microstructure comprenant une phase de zinc primaire et des phases eutectiques binaires et/ou eutectiques ternaires, une diffraction de rétrodiffusion d'électrons (EBSD) étant utilisée pour déterminer un exposant (n) de durcissement de contrainte dépendant de l'orientation cristallographique de la microstructure de revêtement d'alliage de zinc.
PCT/EP2020/074218 2019-08-30 2020-08-31 Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique WO2021038102A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
KR1020227010436A KR20220054384A (ko) 2019-08-30 2020-08-31 금속 기판 상의 아연 합금 코팅의 성형 특성을 특성화하는 방법
EP20764085.5A EP4022102A1 (fr) 2019-08-30 2020-08-31 Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP19194662 2019-08-30
EP19194662.3 2019-08-30

Publications (1)

Publication Number Publication Date
WO2021038102A1 true WO2021038102A1 (fr) 2021-03-04

Family

ID=67810506

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2020/074218 WO2021038102A1 (fr) 2019-08-30 2020-08-31 Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique

Country Status (3)

Country Link
EP (1) EP4022102A1 (fr)
KR (1) KR20220054384A (fr)
WO (1) WO2021038102A1 (fr)

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2088219A1 (fr) * 2006-11-10 2009-08-12 JFE Galvanizing&Coating Co., Ltd. Tôle d'acier revêtue d'un alliage zn-al par immersion à chaud et procédé de fabrication de ladite tôle d'acier
JP2010255084A (ja) 2009-04-28 2010-11-11 Jfe Galvanizing & Coating Co Ltd 溶融Ｚｎ系めっき鋼板
WO2013022118A1 (fr) * 2011-08-09 2013-02-14 Ｊｆｅ鋼板株式会社 Feuille d'acier plaquée d'un alliage de zn-al fondu et son procédé de fabrication
EP3369838A1 (fr) 2015-10-26 2018-09-05 Posco Tôle d'acier plaquée d'alliage de zinc présentant une excellente aptitude au cintrage, et son procédé de fabrication
WO2019125020A1 (fr) * 2017-12-24 2019-06-27 주식회사 포스코 Tôle d'acier galvanisée par immersion à chaud ayant d'excellentes aptitude au façonnage et adhérence à basse température et procédé de fabrication s'y rapportant

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2088219A1 (fr) * 2006-11-10 2009-08-12 JFE Galvanizing&Coating Co., Ltd. Tôle d'acier revêtue d'un alliage zn-al par immersion à chaud et procédé de fabrication de ladite tôle d'acier
JP2010255084A (ja) 2009-04-28 2010-11-11 Jfe Galvanizing & Coating Co Ltd 溶融Ｚｎ系めっき鋼板
WO2013022118A1 (fr) * 2011-08-09 2013-02-14 Ｊｆｅ鋼板株式会社 Feuille d'acier plaquée d'un alliage de zn-al fondu et son procédé de fabrication
EP3369838A1 (fr) 2015-10-26 2018-09-05 Posco Tôle d'acier plaquée d'alliage de zinc présentant une excellente aptitude au cintrage, et son procédé de fabrication
WO2019125020A1 (fr) * 2017-12-24 2019-06-27 주식회사 포스코 Tôle d'acier galvanisée par immersion à chaud ayant d'excellentes aptitude au façonnage et adhérence à basse température et procédé de fabrication s'y rapportant

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
A GHOSH AND N P GURAO: "Evolution of deformation heterogeneity at multiple length scales in a strongly textured zinc layer on galvanized steel", IOP CONF. SER.: MATER. SCI. ENG., vol. 82, 2015, pages 1 - 5, XP002794787, DOI: 10.1088/1757-899X/82/1/012024 *
C. TOME: "The yield surface of hcp crystals", ACTA METALL., vol. 33, 1985, pages 603 - 621
DAO ET AL.: "Computational modeling of the forward and reverse problems in instrumented sharp indentation", ACTA MATER., vol. 49, 2001, pages 3899 - 3918, XP002244670, DOI: 10.1016/S1359-6454(01)00295-6
R. PARISOT ET AL.: "Deformation and Damage Mechanisms of Zinc Coatings on Hot-Dip Galvanized Steel Sheets: Part I. Deformation Modes", METALL. MATER. TRANS. A PHYS. METALL. MATER. SCI., vol. 35 A, 2004, pages 797 - 811, XP019694969

Also Published As

Publication number Publication date
EP4022102A1 (fr) 2022-07-06
KR20220054384A (ko) 2022-05-02

Similar Documents

Publication Publication Date Title
CN110268087B (zh) 镀覆钢材
CA2981236C (fr) Methode de production de materiau lamine en alliage d'aluminium destine au moulage ayant une excellente maniabilite de courbure et une resistance a la formation de sillon et comportant un alliage en aluminium
EP3135394B1 (fr) Procédé de fabrication d'un article moulé à la presse à chaud
JP4584179B2 (ja) 耐食性および加工性に優れた溶融Ｚｎ−Ａｌ合金めっき鋼板の製造方法
TWI666341B (zh) 鍍敷鋼板
Pereira et al. Fracture behavior and fatigue performance of Inconel 625
JP5825244B2 (ja) 溶融亜鉛めっき鋼板
JP4431194B2 (ja) 溶接構造用のＡｌ−Ｍｇ合金製品
Safaeirad et al. Effect of microstructure and texture on formability and mechanical properties of hot-dip galvanized steel sheets
EP1905859A1 (fr) Feuille d'acier revetue a systeme sn-zn d'immersion a chaud presentant une bonne resistance a la corrosion
JP2006009140A (ja) 塗装焼付け硬化性に優れた６０００系アルミニウム合金板およびその製造方法
Oskouei et al. An investigation on the fatigue behaviour of Al 7075-T6 coated with titanium nitride using physical vapour deposition process
Wei et al. Wear-induced microstructural evolution of ultra-fine grained (UFGs) aluminum
Nakai et al. The effect of microstructure on mechanical properties of forged 6061 aluminum alloy
Kim et al. Deformation behavior and texture formation in AZ80 magnesium alloy during uniaxial compression deformation at high temperatures
Kaiser et al. Influence of rolling conditions on the microstructure and mechanical properties of magnesium sheet AZ31
TW201432091A (zh) 熔融Ａｌ－Ｚｎ系鍍覆鋼板及其製造方法
Lonyuk et al. Effect of high-phosphorus electroless nickel coating on fatigue life of Al–Cu–Mg–Fe–Ni alloy
TWI792602B (zh) 鍍敷鋼材
WO2021038102A1 (fr) Procédé de caractérisation de propriétés de formabilité d'un revêtement d'alliage de zinc sur un substrat métallique
WO2020213680A1 (fr) Matériau en acier plaqué
JP5907323B1 (ja) 高強度溶融亜鉛めっき鋼板
Rao et al. Influence of cold rolling and annealing on the tensile properties of aluminum 7075 alloy
JP2022513692A (ja) ６ｘｘｘアルミニウム合金
Schaufler et al. The influence of hydrogenated amorphous carbon coatings (aC: H) on the fatigue life of coated steel specimens

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 20764085

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 20227010436

Country of ref document: KR

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 2020764085

Country of ref document: EP

Effective date: 20220330