A difração de raios X e de elétrons retroespalhados, em escalas distintas, foram aplicadas para acompanhar mudanças microestruturais em dois aços ferríticos baixo carbono (2%Si e ABNT 1006), observando-se o desenvolvimento da textura nas etapas de laminação a frio (skin-pass) e recozimento a 760 oC. Para ambos os aços, os resultados permitiram afirmar que o fenômeno que ocorre após a laminação por skin-pass e tratamento térmico, nas condições deste trabalho, é a recristalização primária. A aplicação do skin-pass criou mais discordâncias em grãos com baixo fator de Taylor por sofrerem mais deformações. Observou-se a nucleação e crescimento de grãos em regiões de grande densidade de células de discordâncias. A presença do silício atrasou a recuperação favorecendo o aumento de subcontornos. Não foi observado o crescimento anormal de grãos, nem em função da presença de grãos Goss. Os contornos CSL não garantiram o crescimento do grão. Núcleos de crescimento de grãos deram origem a grãos com orientações distintas, indicando que o crescimento de grãos não dependeu da existência prévia de grãos com as orientações desenvolvidas, demonstrando que o crescimento anormal de grãos não está relacionado necessariamente com os grãos Goss. / X ray and electron backscattering diffraction, in distinct levels, were applied to evaluate microstructural changes in two low carbon ferritic steels (2%Si and ABNT 1006), observing the texture development in cold lamination step (skin-pass) and in the subsequent annealing at 760 oC. In these two steels, results showed that after the skin-pass and annealing in the conditions of the present work, the observed phenomenon is the primary recrystallization. By applying skin-pass dislocations were introduced mostly in low Taylor factor grains as they are prone to be more deformed. Nucleation and grain growth were observed in high density dislocation cell regions. Silicon presence delayed the recovery favoring the sub-boundaries increase. It was not observed the abnormal grain growth, even in the presence of Gross grains. CSL boundaries did not guarantee the grains growth. Growing nuclei gave rise to grains with distinct orientations, showing that the grain growth was not dependent on the previous presence of grains with the developed orientation. This fact demonstrates that the abnormal grain growth is not necessarily related to the Gross grains.

Este trabalho tem como objetivo caracterizar as mudanças microestruturais durante o recozimento isotérmico de um fio de ferro trefilado a frio e de pureza comercial com ênfase no crescimento de grão. Os recozimentos foram realizados no intervalo de 823-1173 K por diversos tempos. As informações estatísticas do tamanho de grão foram obtidas por meio do método dos interceptos lineares. O mapeamento das orientações foi obtido por meio de difração de elétrons retroespalhados (EBSD). O material apresenta uma microestrutura ferrítica e totalmente recristalizada a partir de 873 K. Foram encontrados indícios de crescimento normal de grão a partir de 1023 K, porém este crescimento não evoluiu consideravelmente ao longo do tempo de tratamento. Os resultados obtidos a partir do método dos interceptos lineares demonstram que a distribuição de tamanho de grão segue uma curva próxima à log-normal. Nas amostras recozidas a partir de 1123 K, verificou-se a ocorrência de crescimento anormal de grão. O crescimento anormal de alguns grãos inicia-se na região central do fio, estendendo-se até uma região próxima à superfície do fio. Algumas modificações na dimensão da amostra e na atmosfera de recozimento foram realizadas a fim de se estudar a interação destas variáveis no desenvolvimento dos grãos anormais. Foram identificados indícios morfológicos de que o mecanismo para ocorrência de crescimento anormal foi o molhamento de contornos no estado sólido (solid-state wetting) que depois foram confirmados pelas análises de micro e mesotexturas. A análise de microtextura também revela que o material apresenta duas componentes preferenciais, as fibras || DT e || DT, onde DT é a direção axial de trefilação. A primeira orientação é a mais intensa, sendo que seu fortalecimento parece ser impulsionado pelo crescimento anormal de grão. A segunda é menos intensa e parece estar relacionada com as orientações dos grãos oriundos da recristalização primária. Aspectos teóricos e analíticos sobre o crescimento de grão são apresentados e associados aos resultados experimentais e à literatura. / This Dissertation aims follow the microstructural changes occurring during isothermal annealing of commercially-pure cold-drawn iron wire, with emphasys on grain growth phenomena. The grain size data were obtained by means of the linear intercept method. The orientations scanning were done by means of electron backscatter diffraction patterns (EBSD). Isothermal annealing was performed within the temperature range 823 - 1173 K for several times. The material displays full recrystallization at temperatures above 873 K. Normal grain growth was observed above 1023 K, although this growth did not evolve through longer annealing times. The results of the linear intercept method show the grain size distribution has a log-normal shape. For samples annealed above 1123 K, abnormal grain growth occurs. The first signs of secondary recrystallization appear close to the center of the wire, growing towards the surface. Changes in the wire diameter and annealing atmosphere were performed to assess the effect of these variables on abnormal grain growth. Results point out that abnormal grain growth is driven by solid-state wetting. These morphological observations were also confirmed by micro and mesotexture analyses. The microtexture also shows the presence of two major fiber texture components || WD and || WD, were WD is the axial wire-drawn direction. The first one is the most intense and its strengthening seems to be related with abnormal grain growth. The second one is weaker and it seems to be most related with small primary recrystallized grains. Theoretical and analytical features about grain growth are presented and discussed in light of literature and experimental results.

Os aços inoxidáveis dúplex possuem uma estrutura bifásica (ferrita e austenita) geralmente em frações aproximadamente iguais. Devido aos altos teores de Cr e Ni, esses aços apresentam alta resistência à corrosão e, por isso, são usados principalmente nas indústrias química, petroquímica e nuclear. Dependendo da sua composição química, os aços dúplex podem sofrer transformação martensítica induzida por deformação, com a transformação de austenita (γ) em martensita (α\'). Essa transformação pode ser revertida mediante tratamento térmico. A austenita é paramagnética, enquanto que a ferrita e a martensita são ambas ferromagnéticas. O objetivo desse trabalho foi estudar a relação entre a estabilidade microestrutural e as propriedades magnéticas de um aço dúplex UNS S32304, o qual apresenta transformação martensítica induzida por deformação. Amostras desse aço com redução em espessura de 80% foram recozidas isotermicamente em várias temperaturas até 800ºC por 1 h e resfriadas em água. A partir de laços de histerese obtidos em temperatura ambiente foram obtidos os valores de magnetização de saturação (Ms) e campo coercivo (Hc) para essas amostras. Além das medidas magnéticas essas amostras foram caracterizadas via difração de raios X, testes de dureza, microscopias óptica (MO) e eletrônica de varredura (εEV). Em relação ao εEV foram utilizadas as técnicas de EBSD (do inglês \"eléctron backscatter diffraction\") e ECCI (do inglês \"electron channeling contrast imaging\"). Medidas de magnetização (in situ) em função da temperatura (até 1000ºC) também foram obtidas para o material deformado, a partir das quais foi determinada a temperatura de Curie (Tc) do mesmo. Uma simulação das fases presentes no material em função da temperatura foi obtida utilizando-se o software Thermo-Calc©. Para as amostras recozidas isotermicamente, a inspeção metalográfica mostrou que para 600-700ºC o material apresenta um aspecto fragmentado na microestrutura. Esse aspecto fragmentado é uma evidência da reversão da martensita em austenita. Para a amostra recozida em 700ºC precipitados foram encontrados principalmente na austenita, a qual parece estar recristalizada. Indícios de recristalização da ferrita também foram observados para essa amostra. De acordo com o Thermo-Calc© os precipitados observados são provavelmente do tipo M23C6 (M = Fe, Cr) e Cr2N. A dureza do material apresenta uma queda evidente a partir de 500ºC, relacionada aos fenômenos de recristalização do material e reversão da martensita. Tal como a dureza, Ms e Hc também decaem a partir de ~ 500ºC. A reversão da martensita em austenita e a decomposição da ferrita (α) contribuem para a diminuição de Ms. As medidas magnéticas in situ também forneceram evidências da transformação α → γ + precipitados a partir do comportamento de Tc. Apesar do aspecto fragmentado da microestrutura e da precipitação, não foi observado um comportamento de \"pico\" em Hc em consequência da reversão da martensita em austenita. Isso indica que, no presente estudo, o fator que mais influenciou Hc foi a maior mobilidade das paredes de domínios magnéticos na fase ferrítica, em consequência dos efeitos de recuperação e recristalização. / Duplex stainless steels have a two-phase structure (ferrite and austenite) in approximately equal fractions. Due to their high Cr and Ni contents, these steels present a high corrosion resistance and, in consequence, they are mainly used in chemical, petrochemical and nuclear industries. Depending on their chemical composition, duplex steels may undergo strain induced martensite, with the austenite (γ) transformation in martensite (α\'). This transformation can be reversed by annealing. The austenite is paramagnetic, whereas ferrite and martensite are both ferromagnetic. The goal of this work was to study the relationship between microstructural stability and magnetic properties of a UNS S32304 duplex steel, which presents strain induced martensite. Samples of this steel with 80% thickness reduction were isotermally annealed at several temperatures up to 800ºC for 1 h and water-cooled. From hysteresis loops taken at room temperature, both saturation magnetization (Ms) and coercive field (Hc) were obtained for these samples. In addition to magnetic measurements these samples were characterized using X-ray diffraction, hardness testing, optical (OM) and scanning electron (SEM) microscopies. Regarding SEM were used both EBSD (eléctron backscatter diffraction) and ECCI (electron channeling contrast imaging) techniques. In situ magnetization measurements in function of temperature (up to 1000ºC) were also performed for the deformed material, from which was determined its Curie temperature (Tc). A simulation of the phases present in the material as a function of temperature was performed using the Thermo-Calc© software. For the isothermally annealed samples, metallographic analysis showed that for 600-700ºC the material presents a fragmented microstructure. Such fragmentation is an evidence of the martensite-to-austenite reversion. For the sample annealed at 700ºC precipitates were found mainly in the austenitic phase, which appears to be recrystallized. Evidences of recrystallization were also found for the ferritic phase in the same sample. According to Thermo-Calc© the observed precipitates are probably M23C6 (M = Fe,Cr) and Cr2N. Material\'s hardness present an evident drop for temperatures higher than 500ºC, due to both recrystallization and martensite-to-austenite reversion phenomena. Like hardness, both Ms and Hc also drop in temperatures higher than 500ºC. The martensite-toaustenite reversion and the ferrite decomposition contribute to Ms decreasing. From the Tc behavior, the in situ magnetic measurements also provided evidences of the transformation α → γ + precipitates. In spite of microstructure fragmentation and precipitation, it was not observed a \"pick\" effect in Hc behavior as a consequence of the martensite-to-austenite reversion. This indicates that, in the present study, the factor that most influenced Hc was the higher mobility of magnetic domain walls in the ferritic phase, due to both recovery and recrystallization effects.

Le présent programme de recherche constitue une tentative d’expliquer les mécanismes de transformation contrôlant la transformation de la texture qui a lieu lors des opérations technologiques du recuit. Les expériences ont été conduites sur les échantillons monocristallins dont les orientations étaient dites « stables »: Goss{110}<001> et ‘brass’{110}<112>, déformées jusqu’à la plage des degrés importants de déformation lors de l’essai de compression encastrée modélisant le processus de laminage. Ensuite les échantillons ont été soumis au recuit à des températures situées dans le domaine de recristallisation primaire. L’analyse des transformations cristallographiques a été menée sur des métaux représentant un large spectre d’énergie du défaut d’empilement : petite - Cu-2% Al, moyenne - Cu et Ni grande - Al et Al-1%Mn. Lors du travail on a analysé les mécanismes de contrôle des phases initiales de recristallisation. L’analyse détaillée de la désorientation à travers le front de recristallisation a montré clairement que les orientations initiales des grains n’étaient pas dues au hasard. Les axes de désorientation dans la relation à travers le front de recristallisation se trouvaient près des normales aux plans {111}, mais ne se recouvraient que sporadiquement avec la direction <111>. La distribution de l’angle de rotation en relation à travers le front de recristallisation présentait les préférences à la formation de deux maxima : près des valeurs 30° et 45-55°. / The present research program is a renewed attempt at explaining the transformation mechanisms. The experimental investigations has focused on a model analysis of transformations which occur in single crystals, with stable orientations, i.e. Goss{110}<001> and brass{110}<112>, the deformation is carried out by channel-die compression to simulate the rolling process of thin sheets. Next, the samples were annealed at temperatures of primary recrystallization. The analysis of crystallographic transformations was conducted on metals from a wide spectrum of stacking fault energy: low – Cu-2%Al, average- Cu and Ni to high Al and Al-1%Mn. At work were analyzed the mechanisms controlling the initial stages of recrystallization. Detailed analysis of disorientation across the recrystallization front clearly showed that the initial grain orientations were not accidental. The axes of disorientation in the relationship across the front of recrystallization were near normal in {111} planes, but only sporadically covered with the <111> direction. The distribution of the recrystallization angle rotation in relation to the preferences presented through the formation of two maxima values near 30 ° and 45-55 °.

A difração de raios X e de elétrons retroespalhados, em escalas distintas, foram aplicadas para acompanhar mudanças microestruturais em dois aços ferríticos baixo carbono (2%Si e ABNT 1006), observando-se o desenvolvimento da textura nas etapas de laminação a frio (skin-pass) e recozimento a 760 oC. Para ambos os aços, os resultados permitiram afirmar que o fenômeno que ocorre após a laminação por skin-pass e tratamento térmico, nas condições deste trabalho, é a recristalização primária. A aplicação do skin-pass criou mais discordâncias em grãos com baixo fator de Taylor por sofrerem mais deformações. Observou-se a nucleação e crescimento de grãos em regiões de grande densidade de células de discordâncias. A presença do silício atrasou a recuperação favorecendo o aumento de subcontornos. Não foi observado o crescimento anormal de grãos, nem em função da presença de grãos Goss. Os contornos CSL não garantiram o crescimento do grão. Núcleos de crescimento de grãos deram origem a grãos com orientações distintas, indicando que o crescimento de grãos não dependeu da existência prévia de grãos com as orientações desenvolvidas, demonstrando que o crescimento anormal de grãos não está relacionado necessariamente com os grãos Goss. / X ray and electron backscattering diffraction, in distinct levels, were applied to evaluate microstructural changes in two low carbon ferritic steels (2%Si and ABNT 1006), observing the texture development in cold lamination step (skin-pass) and in the subsequent annealing at 760 oC. In these two steels, results showed that after the skin-pass and annealing in the conditions of the present work, the observed phenomenon is the primary recrystallization. By applying skin-pass dislocations were introduced mostly in low Taylor factor grains as they are prone to be more deformed. Nucleation and grain growth were observed in high density dislocation cell regions. Silicon presence delayed the recovery favoring the sub-boundaries increase. It was not observed the abnormal grain growth, even in the presence of Gross grains. CSL boundaries did not guarantee the grains growth. Growing nuclei gave rise to grains with distinct orientations, showing that the grain growth was not dependent on the previous presence of grains with the developed orientation. This fact demonstrates that the abnormal grain growth is not necessarily related to the Gross grains.

No presente trabalho estudou-se a recristalização do aço de alta resistência baixa liga (ARBL) microligado ao nióbio (160 ppm em peso) da Companhia Siderúrgica Nacional 2336 utilizado na fabricação de reforços estruturais para a indústria automobilística. A grande utilização deste tipo de aço pelas indústrias tem motivado o desenvolvimento de novas ligas capazes de atender a requisitos críticos de estampagem combinado com alta resistência mecânica. Amostras deste aço no estado laminado a quente foram deformadas posteriormente a frio em escala piloto com reduções de 50 e 70%, reduções típicas na indústria, e recozidas em banho de sal em temperaturas variando entre 600 e 700ºC em diferentes tempos. A evolução microestrutural das amostras no estado encruado e na condição recozida foi acompanhada utilizando-se as técnicas de microscopia ótica e eletrônica de varredura. As texturas de deformação e de recristalização foram determinadas via difração de raios X. A fração volumétrica recristalizada (Xv) e o tamanho de grão foram determinados com o auxílio de metalografia quantitativa nas amostras recozidas. Medidas de microdureza Vickers foram utilizadas para construir as curvas de encruamento e da cinética de amolecimento em função da temperatura de recozimento e comparadas com curvas construídas pelo primeiro método. Os resultados mostram que a recristalização ocorre em temperaturas acima de 650°C. Com auxílio de um gráfico de Xv contra A (fração amolecida), podemos observar a ocorrência de um desvio da idealidade a 650°C e 700°C. A explicação mais provável é a ocorrência de precipitação, especialmente para o aço menos deformado. Os valores do expoente de Avrami obtidos a partir das duas abordagens (medidas de microdureza e metalografia quantitativa) são apresentados e discutidos. / The recrystallization of a high strength low alloy steel (HSLA) containing niobium (160 wt-ppm) was investigated. The HSLA steel, named CSN 2336, is used in the manufacture of structural parts for automotive industry. The increasing use of this application type of steels in automotive industries has motivated the development of new alloys able to gather the critical requirements for deep drawing combined with high strengths. Samples of this steel in hot-rolled condition were cold-rolled with reductions of 50% and 70%, commonly used in most of applications, and isothermally annealed in salt bath at temperatures between 600 and 700ºC. The microstructure of the samples in both coldworked and annealed states was imaged using light optical (LOM) and scanning electronic microscopies (SEM). Deformation and recrystallization textures were determined by X-ray diffraction. The recrystallized volume fraction (Xv) and the mean grain size were determined by quantitative metallography in the annealed samples. Vickers microhardness testing was used to determine the work hardening and the softening kinetics behaviors. The results show that recrystallization occurs at temperatures above 650°C for the most deformed steel. By plotting Xv against A (softening fraction), we observe the occurrence of a deviation from ideality at 650°C and 700°C, likely caused by solid-state precipitation, especially for the less deformed steel. The values of n (Avrami exponent) obtained from both approaches (softening curves and quantitative metallography) are presented and discussed.

Le présent travail concerne l’étude de l’usinage de l’alliage de titane Ti-6Al-4V, matériau très apprécié par les industries aéronautique, biomédicale et de l’énergie. Les qualités des alliages de titane sont nombreuses : haute résistance aux températures élevées et à la corrosion, haute résistance mécanique, biocompatibilité, etc. Cependant, certaines propriétés physiques de ces matériaux, comme leur faible conductivité thermique, conduisent à des difficultés lors de leur mise en forme par usinage. Des études ont été et sont toujours conduites afin de comprendre le comportement de ces matériaux lors de leur mise en forme. Peu de travaux portent sur la prise en compte de la microstructure dans le comportement des alliages de titane lors du procédé d’usinage. Cette dimension constitue l’une des originalités de ce travail de thèse. Les phénomènes microstructuraux sont caractérisés à travers une étude expérimentale en coupe orthogonale de l’alliage Ti-6Al-4V. Les efforts, la température, la morphologie des copeaux et la microstructure sont analysés et interprétés. Une étude numérique du processus de coupe par simulation éléments finis est employée pour comprendre le rôle de l’endommagement et de la recristallisation. A partir des conclusions de ces différentes études, la construction d’un nouveau modèle de comportement est proposée. Ce modèle est appliqué à une modélisation élément fini pour différentes conditions de coupe afin d’étudier l’influence des paramètres d’usinage. Le modèle est validé par comparaison aux résultats expérimentaux. Il est ensuite exploité afin de proposer une analyse du processus de la coupe et notamment de la formation du copeau. / The present work concerns the study of the machining of titanium alloy Ti-6Al-4V. This material is much appreciated by the aerospace, biomedical and energy industries for its advantageous properties: high resistance to high temperatures and corrosion, high mechanical strength, biocompatibility, etc. However, certain physical properties of these materials, such as their low thermal conductivity, lead to difficulties during the machining process. Studies have been and are still conducted to understand the behavior of these materials during their shaping. Few studies consider the influence of microstructure on the behavior of titanium alloys during the machining process. This is one of the originalities of the present work. The microstructural phenomena are characterized through an experimental study of orthogonal cutting of the Ti-6Al-4V alloy. Machining forces, temperature, chip morphology and microstructure are analyzed and discussed. A numerical study of the finite element simulation process is used to understand the role of damage and recrystallization. From the conclusions of these different studies, the construction of a new model of behavior is proposed. This model is applied to finite element modeling for different cutting conditions to study the influence of machining parameters. The model is validated by comparison with the experimental results. It is then used to propose an analysis of the microstructural phenomena during the cutting process and the formation of the chip.

AA6061 Al alloys modified with addition of Mn, Cr and Cu were homogenized at temperatures between 350 ºC and 550 ºC after casting. STEM experiments revealed that the formation of α-Al(MnFeCr)Si dispersoids during homogenization were strongly affected by various factors such as heating rate, concentration of Mn, low temperature pre-nucleation treatment and homogenization temperature. Through analysis of the STEM results using an image software Image-Pro, the size distributions and number densities of the dispersoids formed during different annealing treatments were quantitatively measured. It was revealed that increasing the heating rate or homogenization temperature led to a reduction of the number density and an increase in size of the dispersoids. The number density of dispersoids could be markedly increased through a low temperature pre-nucleation treatment. A higher Mn level resulted in the larger number density, equivalent size and length/width ratio of the dispersoids in the alloy. Upsetting tests on two of these Mn and Cr-containing AA6061 (Al-Mg-Si-Cu) Al alloys with distinctive Mn contents were carried out at a speed of 15 mm s-1 under upsetting temperature of 450 ºC after casting and subsequent homogenization heat treatment using a 300-Tone hydraulic press. STEM experiments revealed that the finely distributed α-Al(MnFeCr)Si dispersoids formed during homogenization showed a strong pinning effect on dislocations and grain boundaries, which could effectively inhibit recovery and recrystallization during hot deformation in the two alloys. The fractions of recrystallization after hot deformation and following solution heat treatment were measured in the two alloys with EBSD. It was found that the recrystallization fractions of the two alloys were less than 30%. This implied that the finely distributed α-dispersoids were rather stable against coarsening and they stabilized the microstructure by inhibiting recovery and recrystallization by pinning dislocations during deformation and annealing at elevated temperatures. By increasing the content of Mn, the effect of retardation on recrystallization were further enhanced due to the formation of higher number density of the dispersoids. STEM and 3-D atom probe tomography experiments revealed that α-Al(MnFeCr)Si dispersoids were formed upon dissolution of lathe-shaped Q-AlMgSiCu phase during homogenization of the modified AA6061 Al alloy. It was, for the first time, observed that Mn segregated at the Q-phase/matrix interfaces in Mn-rich regions in the early stage of homogenization, triggering the transformation of Q-phase into strings of Mn-rich dispersoids afterwards. Meanwhile, in Mn-depleted regions the Q-phase remained unchanged without segregation of Mn at the Q-phase/matrix interfaces. Upon completion of α-phase transformation, the atomic ratio of Mn and Si was found to be 1:1 in the α-phase. The strengthening mechanisms in the alloy were also quantitatively interpreted, based on the measurements of chemical compositions, dispersoids density and size, alloy hardness and resistivity as a function of the annealing temperature. This study clarified the previous confusion about the formation mechanism of α-dispersoids in 6xxx series Al alloys. Four-point bend fatigue tests on two modified AA6061 Al alloys with different Si contents (0.80 and 1.24 wt%, respectively) were carried out at room temperature, f = 20 Hz, R = 0.1, and in ambient air. The stress-number of cycles to failure (S-N) curves of the two alloys were characterized. The alloys were solution heat treated, quenched in water, and peak aged. Optical microscopy and scanning electron microscopy were employed to capture a detailed view of the fatigue crack initiation behaviors of the alloys. Fatigue limits of the two alloys with the Si contents of 0.80 and 1.24 wt% were measured to be approximately 224 and 283.5 MPa, respectively. The number of cracks found on surface was very small (1~3) and barely increased with the applied stress, when the applied stress was below the yield strength. However, it was increased sharply with increase of the applied stress to approximately the ultimate tensile strength. Fatigue crack initiation was predominantly associated with the micro-pores in the alloys. SEM examination of the fracture surfaces of the fatigued samples showed that the crack initiation pores were always aspheric in shape with the larger dimension in depth from the sample surface. These tunnel-shaped pores might be formed along grain boundaries during solidification or due to overheating of the Si-containing particles during homogenization. A quantitative model, which took into account the 3-D effects of pores on the local stress/strain fields in surface, was applied to quantification of the fatigue crack population in a modified AA6061 Al alloy under cyclic loading. The pores used in the model were spherical in shape, for simplicity, with the same size of 7 μm in diameter. The total volume fraction of the pores in the model were same as the area fraction of the pores measured experimentally in the alloy. The stress and strain fields around each pore near the randomly selected surface in a reconstructed digital pore structure of the alloy were quantified as a function of pore position in depth from the surface using a 3-D finite element model under different stress levels. A micro-scale Manson-Coffin equation was used to estimate the fatigue crack incubation life at each of the pores in the surface and subsurface. The population of fatigue cracks initiated at an applied cyclic loading could be subsequently quantified. The simulated results were consistent with those experimentally measured, when the applied maximum cyclic stress was below the yield strength, but the model could not capture the sudden increase in crack population at UTS, as observed in the alloy. This discrepancy in crack population was likely to be due to the use of the spherical pores in the model, as these simplified pores could not show the effects of pore shape and their orientations on crack initiation at the pores near surface. Although it is presently very time-consuming to calculate the crack population as a function of pore size and shape in the alloy with the current model, it would still be desirable to incorporate the effects of shape and orientation of the tunnel-shaped pores into the model, in the future, in order to simulate the fatigue crack initiation more accurately in the alloy.

Les aciers Dual-Phase (DP) sont des aciers à très haute résistance mécanique (AHSS) fortement utilisés pour des applications automobiles en raison de leur très bon compromis résistance mécanique/ductilité ainsi que par leur habilité à répondre aux multiples exigences industrielles (bas prix, assemblage, revêtement etc.). A l'heure actuelle, le développement d'aciers DP apparait durable pour la caisse-en-blanc des structures automobiles. La microstructure ferrite-martensite, caractéristique des aciers DP, est obtenue par un traitement thermique complexe composé de différentes étapes au cours desquelles différents mécanismes métallurgiques entrent en jeux. Les principales difficultés de production sont liées au fait (i)que les évolutions microstructurales sont influencées par les différents paramètres de traitement thermique (vitesse de chauffe, température ...), (ii) que les différentes étapes de traitement sont interconnectées et que (iii) les évolutions microstructurales peuvent se chevaucher et, part conséquent, interagir entre elles. Ces travaux de thèse ont pour objectif d'améliorer la compréhension des évolutions métallurgiques entrant en jeux lors des traitements thermiques des aciers DP, et notamment d'améliorer la compréhension de l'influence des paramètres de traitement. Les différentes évolutions métallurgiques ont été, dans un premier temps, caractérisées en couplant un ensemble de techniques expérimentales (dilatométrie, dureté, TPE ...) et grâce à un protocole assurant de décorréler les mécanismes se superposant et interconnectés. A titre d'exemple, les deux principaux mécanismes entrant en jeux lors de l'étape de recuit intercritique ont été, dans un premier temps, étudiés séparément ((1) la recristallisation a été étudié en dessous de la température de formation d'austénite et (2) la formation d'austénite a été étudié sur un acier pré-recristallisé) avant de se concentrer sur le cas des aciers laminés à froid où la recristallisation et formation d'austénite se superposent. Le projet avait également pour objectif de développer des outils de prédictions permettant de décrire les évolutions microstructurales basés sur des approches empiriques (loi de JMAK) ainsi que vers des modèles à base plus physique (mixed-mode modèle et modèle diffusif). Une attention particulière a été dédié à discuter de la fiabilité, l'adaptabilité, des forces et limitations des différentes approches développées. / Dual-Phase steels (DP) are one of the most used Advanced High Strength Steels (AHSS) for automotive applications because they present good strength/ductility compromise and they adapt to number of industrial constraints (low price, shaping, welding, coating etc.). Nowadays, the development of DP steels seems to be promising and sustainable for the body-in-white structure. The typical ferrite-martensite microstructure, characteristic of DP steels, are obtained by a thermal treatment composed of different stages during which metallurgical evolutions occur. Major difficulties of their processing are due to the fact that (i) microstructural evolution kinetics are influenced by cycle parameters (heating rate, annealing temperature etc.), (ii) different stages are interconnected and (iii) some microstructural evolutions may overlap and, therefore, interact. This PhD-work aimed at getting a better understanding of microstructural evolutions during the thermal cycle of DP steel and, namely, the influence of cycle parameters. Different microstructural evolutions occurring during the thermal cycle were first characterized coupling different experimental techniques (dilatometry, hardness, TPE etc.) and with a particular protocol in order to decorrelate overlapping and interconnected phenomena. As example, two major evolutions occurring during the intercritical annealing were first studied individually ((1) recrystallization was investigated below austenite formation temperature and (2) austenite formation was investigated on prior recrystallized steels) before investigated cold-rolled steel case where recrystallization and austenite formation overlap. The study was then attached to develop some predictive tools to describe microstructural evolutions based on phenomenological approaches (JMAK law) towards more physical based models (mixed-mode, diffusive models). A particular care was attached to discuss on model reliability, versatility, strengths and limitations.

Dilute Mg alloys are exclusively identified for wrought structural applications in automotive industry. Any improvement in mechanical properties of alloys is possible only by grain size refinement and by the development of suitable texture. The grain size, grain size anisotropy and texture in these alloys affect the compatibility stresses in a very complex manner. To launch a full scale study towards understanding the complex deformation mechanisms operating in these alloys, it is necessary to understand the effect of grain size and texture on the mechanical behavior of Mg alloys in a broad or semi-quantitative manner first. Current literature lacks such broad study. In this present study, the effect of grain size, grain size anisotropy and texture evolution on the mechanical properties are examined in order to develop an understanding of the deformation mechanism that control the mechanical properties of a dilute conventionally extruded Mg alloy, AZ21. The approach adopted was to first study the microstructure and texture evolution in this conventionally extruded alloy. Since the grain sizes in these alloys vary over a wide range, it is hence necessary to study the microstructure evolution in a highly quantitative manner. In understanding texture, the present study is only limited to qualitatively evaluating the evolution of fibre component of texture using X-Ray Diffraction spectra. For truly quantitative microstructure evolution results in materials were grains sizes are spread over a wide range, it is critical to study a statistically enough no. of grains. Hence to avoid any sampling error, large montages (about 0.3 sq. mm) were constructed out of a series of high resolution images captured using an optical microscope. The montages so constructed are subjected to extensive image enhancement and various other operations are performed to convert these coloured to binary montages. Information like grain size, diameter etc., can be easily extracted from these binary montages and used for further analysis. Fibre texture in these conventionally extruded dilute Mg alloys generally develops due to alignment of basal planes along the direction of extrusion. The Critical Resolved Shear Stress for basal slip is very low when compared to that of non-basal planes. And also since there are very limited primary slip systems in these dilute Mg alloys, the development of strong fibre texture drastically changes the compatibility stresses and hence the mechanical properties . To broadly study the effect of microstructure-texture on mechanical proerties, after post extrusion annealing, heat treatments representing typical microstructure-texture combinations were identified. Effect of each microstructure-texture combination on the tensile and completely reversed cyclic fatigue properties are studied and qualitatively interpreted. The fibre texture showed pronounced effect on tensile ductility but it hardly affected the yield strength. With just 10% reduction in BPI, the ductility reduced by about 50%. A small change in average grain size did not alter the yield strength. Unlike tensile ductility, fatigue endurance stress was not altered drastically by the change in grain size or texture. But there appeared to be a significant effect of residual stress. In ending, a small change in microstructure-texture combination in these conventionally extruded alloys has a pronounced effect on ductility or in other words plastic properties. But a it has minimal effect on yield strength and fatigue endurance stress.