A seven-element Modified Embedded Atom Method (MEAM) potential comprising Fe, Mn, Si, C, Al, Zn, and O is developed by employing a hierarchical multiscale modeling paradigm to simulate low-alloy steels, inhibition layer, and galvanized coatings. Experimental information alongside first-principles calculations based on Density Functional Theory served as calibration data to upscale and develop the MEAM potential. For calibrating the single element potentials, the cohesive energy, lattice parameters, elastic constants, and vacancy and interstitial formation energies are used as target data. The heat of formation and elastic constants of binary compounds along with substitutional and interstitial formation energies serve as binary potential calibration data, while substitutional and interstitial pair binding energies aid in developing the ternary potential. Molecular dynamics simulations employing the developed potentials predict the thermal expansion coefficient, heat capacity, self-diffusion coefficients, thermomechanical stress-strain behavior, and solid-solution strengthening mechanisms for steel alloys comparable to those reported in the literature. Interfacial energies between the steel substrate, inhibition layer, and surface oxides shed light on the interfacial nanostructures observed in the galvanizing process.

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Les revêtements GalvAnnealed (GA), constitués de phases Fe-Zn, sont utilisés pour protéger les aciers contre la corrosion. Ces revêtements sont réalisés en trois étapes principales: le recuit de recristallisation, l'immersion dans un bain de zinc contennant de 0,11 à 0,13% poids d'aluminium et le traitement thermique du revêtement de zinc. Lors de la première étape, l'oxydation sélective des éléments d'alliage se produit à la surface de l'acier. Dans le cas des aciers chargés en éléments d'alliage (TRansformation Induced-Plasticity), les oxydes sélectifs sont connus pour créer des problèmes de réactivité entre l'acier et le zinc liquide. L'état d'oxydation sélective dépend du point de rosée (PR) de l'atmosphère de recuit. La formation du revêtement Fe-Zn implique des réactions complexes: la formation de la couche d'inhibition, sa rupture, la consommation du zinc et l'enrichissement en fer. Dans ce travail, l'effet du PR de l'atmosphère de recuit sur l'oxydation sélective et la formation du revêtement sur un acier TRIP MnAl a été étudié. Il a été montré que l'atmosphère de recuit influe principalement sur la morphologie (films ou nodules) et la localisation des oxydes par rapport à la surface de l'acier (externe / interne). Les résultats expérimentaux sont en accord avec les calculs thermodynamiques. Indépendamment du PR, la couche d'inhibition est constituée de deux phases, δ (FeZn7) et Fe2Al5Znx. Les oxydes externes formés lors du recuit sont incrustés dans ces phases. La couche d'inhibition ne bloque les réactions Fe-Zn que temporairement. Lors du traitement galvannealing, la rupture de la couche d'inhibition se produit par deux mécanismes réactionnels qui dépendent de l'état d'oxydation sélective. Globalement, les films d'oxyde (bas PR) incrustés dans la couche d'inhibition ont un effet retardateur sur les réactions Fe-Zn par rapport aux oxydes nodulaires (haut DP). / GalvAnnealed (GA) coatings, composed of Fe-Zn phases, are used to protect steels against corrosion. These coatings are produced in three main steps, namely recrystallization annealing, immersion in a zinc bath with 0.11 to 0.13 wt.% aluminum and heat treatment of the zinc coating. In the first step, the selective oxidation of the alloying elements occurs at the steel surface. In the case of high alloyed steels (e.g. TRansformation-Induced Plasticity), the selective oxides are known to be detrimental for the reactions between the steel substrate and liquid zinc. The selective oxidation state depends on the dew point (DP) of the annealing atmosphere. The coating formation involves complex reactions: the inhibition layer formation, its breakdown, the liquid zinc consumption and the iron enrichment. In this work, the effect of the DPof the annealing atmosphere on the selective oxidation and the coating formation on a TRIP MnAl steel was investigated. It was shown that the annealing atmosphere mainly affects the morphology (films or nodules) and the location of the selective oxides with respect to the steel surface (external / internal). The experimental results are in line with the thermodynamic calculations. The inhibition layer is composed of two phases, δ (FeZn7) and Fe2Al5Znx, irrespective of the DP. In addition, it contains the external oxides formed during the first step. The inhibition layer hinders the Fe-Zn reactions only temporarily. Depending on the selective oxidation state, during galvannealing treatment the inhibition layer rupture occurs by two different reaction mechanisms. Globally, the oxide films (low DP) embedded in the inhibition layer, delay the Fe-Zn reactions compared to nodular oxides (high DP).

<p> Aluminum is usually added to the zinc bath to form an Fe-Al interfacial layer which retards the formation of a series of Fe-Zn intermetallic compounds during the hot-dip galvanizing process. However, experimentally exploring the inhibition layer formation and obtaining useful experimental data to understand the mechanisms is quite challenging due to short times involved in this process. In this study, a galvanizing simulator was used to perform dipping times as short as O.ls and rapid spot cooling techniques have been applied to stop the reaction between the molten zinc coating and steel substrate as quickly as possible. In addition, the actual reaction time has been precisely calculated through the logged sample time and temperature during the hot-dipping process. The kinetics and formation mechanism of the inhibition layer was characterized using SEM, ICP and EBSD based on the total reaction time. For bath containing 0.2wt% dissolved AI, the results show that FeA13 nucleates and grows during the initial stage of the inhibition layer formation and then Fe2Als forms by a diffusive transformation. The evolution of the interfacial layer formed in a zinc bath with 0.13wt% dissolved AI, including Fe-Aland Fe-Zn intermetallic compounds, was a result of competing reactions. In the initial period, the Fe-Al reaction dominated due to high thermodynamic driving forces. After the zinc concentration reached a critical composition in the substrate grain boundaries, formation of Fe-Zn intermetallic compounds was kinetically favoured. Fe-Zn intermetallic compounds formed due to zinc diffusing to the substrate via short circuit paths and continuously grew by consuming Fe-Al interfacial layer after samples exited the zinc bath due to the limited Al supply. A mathematical model to describe the formation kinetics as a function of temperature for the 0.2wt% Al zinc bath was proposed. It indicated that the development of microstructure of the interfacial layer had significant influence on the effective diffusion coefficient and growth of this layer. However, the model underestimates the AI uptake by the interfacial layer, particularly at higher temperatures. This is thought to be due to the effect of the larger number of triple junctions in the inhibition layer leading to an underestimation of the effective diffusivity. </p> / Thesis / Master of Science (MSc)

This study is mainly aimed at interstital-free and dual-phase steels, analyzing the compositions and distribution of selective surface oxides after annealing and then to know the influence of these oxidation for the formation of FeAl inhibition layer in hot-dip galvanizing. Interstital-free and dual-phase steels were first annealed at 800 oC for 1-200 s in a 10% H2-N2 protected atmosphere of -70 oC and 0 oC dew point respectively and then dipped in zinc bath with Al content 0.12-0.18 wt% for 0-20 s. Using this combined SEM, Auger electron spectroscopy(AES), X-ray photoelectron spectroscopy(XPS) and ICP-AES etc. instruments, it is shown that the MnAl2O4 spinels were the major oxidation on the surface of IF steel after annealing. The average oxidation thickness was about 5-15 nm. Annealing times has little effect on the thickness. On the other hand, MnO were observed on DP steel surface after anneaing. The MnO paticles mainly distributed at the grain boundaries ,and the average oxdaiton thickness increase rapidly from 20 nm(10 s) to 110 nm(200 s) with annealing times. The growth of the FeAl inhibition layer can separate to nucleation in initial stage and diffusion growth later. The Fe2Al5 nucleation times were all about 0.1 s in both steels , and average thicknesses were approximately 20 nm. For IF steels , Al uptake in the zinc bath and steel interface was depleted in nucleation stage with 0.12 wt% Al content, so that delayed the growth of Fe2Al5, and the rate determining step was the diffusion of Al in zinc bath. When Al content raise up to 0.14 wt%, the phenomenon of growth delay was not happened, and the rate determining step of Fe2Al5 growth changed to the solid-state diffusion of Fe in Fe2Al5. For DP steels, when Al content up to 0.14 wt%, the growth mechanism was similar to IF steels, but the rate determining step of Fe2Al5 growth was mainly in the grain boundary diffusion of Fe in Fe2Al5. Moreover, where the MnO paticles was rich could obviously observe the delay of Fe2Al5 growth. It was probably because of consuming a great deal of Al to reduce the MnO oxides.