The commercial polycrystalline superalloy RR1000 developed for turbine disc applications contains a large number of alloying elements. This complex alloy chemistry is required in order to produce appropriate microstructures and the required mechanical properties, such that the most important strengthener γʹ displays complex alloy chemistry. The broad aim of this project is to develop an approach to measuring the composition of γʹ precipitates at a broad range of length scales from nanometres to hundreds of nanometres, and subsequently develop a better understanding of the role of thermodynamics and diffusion kinetics on γʹ phase separation and precipitate growth. A solution of the absorption-corrected EDX spectroscopy to spherical particles was developed in our work, therefore enabling the quantitative analysis of precipitates' composition using an absorption-corrected Cliff-Lorimer approach. By performing this quantification, size-dependent precipitate compositional variations were obtained. Examination of this quantitative approach was compared to thermodynamic calculations of primary γ' precipitates possessing equilibrium compositions. Given the development of semi-quantitative compositional measurements for spherical γʹ precipitates and that cooling is one of the most common and critical regimes in physical metallurgy of Ni-based superalloys, this approach was then applied to study the local compositional variations that are induced in γ' precipitates when the alloy RR1000 undergoes different cooling rates. These measured compositions have been compared to detailed thermodynamic calculations and provide new experimental evidence of the importance of the dominant role of aluminium antisite diffusion in determining the low-temperature growth kinetics of fine-scale γ' precipitates. We have applied a similar analysis approach to study the compositional variations of γʹ cores within the class of secondary precipitates upon cyclic coarsening and reversal coarsening. It was shown that supersaturated Co in secondary γʹ exhibits an overall trend towards the equilibrium but Co content can significantly increase as γʹ coarsens. It was demonstrated that the limited elemental diffusivity in γ and γʹ compared to the observed coarsening rate in the coarsening regime results in the long-lasting Co supersaturation in γʹ and builds up elemental enhancements or depletions. These inhomogeneous elemental distributions produce compressive elastic constraints on large-scale secondary γʹ, therefore inducing morphological instability of these γʹ and causing the reversal coarsening. These results enable us to better understand the role that both thermodynamics and limited diffusion kinetics plays in controlling the complex microstructures of γ' precipitates.

In this thesis, we consider two models from physics, which are characterized by the interplay of thermodynamical and fluid mechanical phenomena: demixing (spinodal decomposition) and Rayleigh--Bénard convection. In both models, we investigate the dependencies of certain intrinsic quantities on the system parameters. The first model describes a thermodynamically driven demixing process of a binary viscous fluid. During the evolution, the two components of the mixture separate into two domains of the different equilibrium volume fractions. One observes a clear tendency: Larger domains grow at the expense of smaller ones, and thus, the average domain sizes increases --- a phenomenon called coarsening. It turns out that two mechanisms are relevant for the coarsening process. At an early stage of the evolution, material transport is essentially mediated by diffusion; at a later stage, when the typical domain size exceeds a certain value, due to the viscosity of the mixture, a fluid flow sets in and becomes the relevant transport mechanism. In both regimes, the growth rates of the typical domain size obey certain power laws. In this thesis, we rigorously establish one-sided bounds on these growth rates via a priori estimates. The second model, Rayleigh--Bénard convection, describes the behavior of a fluid between two rigid horizontal plates that is heated from below and cooled from above. There are two competing heat transfer mechanisms in the system: On the one hand, thermodynamics favors a state in which temperature variations are locally minimized. Thus, in our model, the thermodynamical equilibrium state is realized by a temperature with a linearly decreasing profile, corresponding to pure conduction. On the other hand, due to differences in the densities of hot and cold fluid parcels, buoyancy forces act on the fluid. This results in an upward motion of hot parcels and a downward motion of cold parcels. We study the dependence of the average upward heat flux, measured in the so-called Nusselt number, on the temperature forcing encoded by the container height. It turns out that the efficiency of the heat transport is independent of the height of the container, and thus, the Nusselt number is a constant function of height. Using a priori estimates, we prove an upper bound on the Nusselt number that displays this dependency --- up to logarithmic errors. Further investigations on the flow pattern in Rayleigh--Bénard convection show a clear separation of length scales: Along the horizontal top and bottom plates one observes thin boundary layers in which heat is essentially conducted, whereas the large bulk is characterized by a convective heat flow. We give first rigorous results in favor of linear temperature profiles in the boundary layers, which indicate that heat is indeed essentially conducted close to the boundaries.

No description available.

We have studied precipitate growth and coarsening in ternary alloys using two different phase held models. The first one is a ternary extension of the classical Cahn-Hilliard (C-H) model in which both the phases are characterized using conserved held variables i.e. composition (cB; cC ); mobility matrix and gradient energy efficient are the other input parameters in this model. In the second model, each phase is treated as separate, and phase identify cation is through a (non-conserved) phase held variable ; we have used a grand potential-based (GP) formulation, due to Plapp [1], Choudhury and Nestler [2], where interfacial energy and interface width, as well as free energy and diffusivity matrix for the relevant phases are the input parameters. The first model i.e. the Cahn-Hilliard (C-H) type model is conceptually simple. The model for ternary is a straight forward extension of the binary. The grand potential (GP) formulation has the advantage of being able to incorporate thermodynamic database like Thermocalc in it. We present below a summary of the findings of our research on (a) precipitate growth, precipitate coarsening, and (c) a critical comparison between results from phase held simulations and those from experiments on an Ni-Al-Mo alloy Precipitate growth In our study of precipitate growth in ternary alloys, we end that when both the solute elements have the same diffusivity, precipitate growth behaviour in ternary alloys is identical to that binary alloys; specifically, we recover the temporal power law r2 = kgt relating the particle radius to time, and the growth kg depends only on supersaturation (i.e., equilibrium volume fraction of the precipitate phase), and is independent of the slope of the tie line. However, when one solute element, (say, C) di uses slower than the other (i.e. (DCC =DBB) < 1,(where DBB, DCC are intertie suavities’ in the lab frame of reference), the ux of C at the interface is smaller than that of species B, causing the precipitate to become depleted in C and enriched in B; this process continues until the growth phase enters a scaling regime where we recover the temporal law for growth: r2 = kgt. In this regime, the tie line selected by the precipitate and matrix interfacial compositions is different from the thermodynamic tie line containing the alloy, a result first reported by Coates [3]. After validating our phase held model quantitatively through a critical comparison with Coates' theory of tie line selection, we have characterized the growth behaviour: specifically, we end that growth kg drops with decreasing value of DCC ; the magnitude of this drop is stronger for alloys which (a) are on higher-C tie lines (i.e., the slope of the tie line is higher), and (b) have smaller precipitate volume fractions. Precipitate coarsening In our simulations, we end that precipitate coarsening does indeed enter a scaling regime where the temporal power law r3 = kt (which relates the average precipitate radius r to (b) time t) is valid; the coarsening rate k depends, as expected, not only on precipitate volume fraction, but also on the slope of the tie line and diffusivity ratio (DCC =DBB). (c) (d) When the solutes have equal diffusivity (i.e., (DCC =DBB) = 1), the coarsening behaviour is essentially the same as that in a binary alloy. However, when solute C (say) is the slower di using species, the coarsening rate k drops, with a deeper drop in alloys on higher-C tie lines. Both these conclusions are similar to those from our study of precipitate growth. (e) (f) However, there is a crucial difference between precipitate growth and coarsening in ternary alloys: The suppression in coarsening rate (for DCC < DBB) in ternary alloys is accompanied by another e ect: larger (and growing) precipitates are richer in the faster di using species B, while the smaller and shrinking precipitates are richer in the slower di using C. In other words, during coarsening in ternary alloys, the tie line selected by precipitate and matrix interfacial components depends on precipitate size; during growth, however, the scaling regime is characterized by the same tie line, independent of precipitate size. (g) (h) (i) Critical comparison between theory and experiment (j) (k) (l) We have used the grand potential based phase held model [1] [2] to study coarsening in Ni-Al-Mo alloys. This model has the advantage of ease with which we can incorporate the thermodynamic and kinetic data on real alloys. (m) (n) A comparison of coarsening rate from our 3D simulations with the experimentally observed rate reveals that diffusivity of the faster di using species (which, in Ni-Al-Mo alloys, is aluminium) from our simulations is within an order of magnitude from the experimental value. However the dominant term in the (@ =@c) matrix is underestimated by 2 to 3 orders of magnitude (compared to its value computed from CALPHAD-based thermodynamic data).

In this dissertation, we study the triangular mesh simplification process, describing its main characteristics. We discuss an adaptation for triangular meshes of a mesh simplification process based on Voronoi coverage proposed by Peixoto [2002]. Moreover, we use Fast Marching Method as a distance function over the mesh and some different strategies for simplified mesh vertices selection, like curvature based selection. The simplification process is done by constructing an intrinsic Voronoi diagram over the original mesh. We discuss some necessary conditions to obtain a mesh, as Voronoi dual, without any singularities and topologically equivalent to the original mesh. / Coordenação de Aperfeiçoamento de Pessoal de Nível Superior / Nesta dissertação, estudaremos o processo de simplificaçãoo de malhas triangulares, caracterizando-o com suas particularidades. Discutiremos uma adaptação para superfícies triangulares do método de simplificação baseado em uma cobertura de Voronoi proposto por Peixoto [2002]. Além disso, utilizaremos o método Fast Marching como uma nova métrica e diferentes estratégias para seleção de vértices da malha simplificada, como a seleção por curvatura. A simplificação ocorre a partir de um diagrama de Voronoi intrínseco à malha. Discutiremos algumas condições necessárias para que a partir do dual desse diagrama, obtenha-se uma malha sem singularidades que seja equivalente a malha original.

Made available in DSpace on 2015-05-14T12:14:03Z (GMT). No. of bitstreams: 1 parte1.pdf: 6372308 bytes, checksum: db3e915edd1663a97d16d8935fc5becf (MD5) Previous issue date: 2012-03-02 / Coordenação de Aperfeiçoamento de Pessoal de Nível Superior - CAPES / In this work we study numerically the generation and dynamics of topological defects in nematic liquid crystals. Our study is based on a Ginzburg-Landau model describing the evolution of the orientational order of a liquid crystal in terms of a symmetric, traceless, second-rank tensor. This phenomenological model allows studies of nematic phases at scales ranging from few nanometers to few micrometers (mesoscopic scale). Within this framework we developed a software named LICRA (Liquid CRystal Algorithm) that combines standard finite difference algorithm for the spatial derivatives with a Runge-Kutta temporal integration to solve the relaxational equations of nematodynamics without thermal fluctuations and hydrodynamic flow. Using this software we investigate the coarsening dynamics of defects of two- and three-dimensional uniaxial nematic liquid crystals. The time dependences of the structure factor and characteristic length scale were computed. The characteristic length scale is expected to grow as a power law in time, L ∝ tα. From dimensional analysis α = 1/2 and we found α = 0, 45±0, 01 in two-dimensions and α = 0, 350±0, 003 in three-dimensions. Furthermore, in all cases Porod s law is satisfied for large values of wave number k. We also investigate, using LICRA, the coarsening dynamics of liquid crystal textures in a two-dimensional nematic under applied electric fields. We consider both positive and negative dielectric anisotropies and two different possibilities for the orientation of the electric field parallel and perpendicular to the two-dimensional lattice. We determine the effect of an applied electric field pulse on the evolution of the characteristic length scale and other properties of the liquid crystal texture network. In particular, we show that different types of defects are produced after the electric field is switched on, depending on the orientation of the electric field and the sign of the dielectric anisotropy. Finally, we present the effect of the rotation of an external electric field on the dynamics of half-integer disclination networks in two and three dimensional nematic liquid crystals with a negative dielectric anisotropy. We show that a rotation of π of the electric field around an axis of the liquid crystal plane continuously transforms all half-integer disclinations of the network into disclinations of opposite sign via twist disclinations. We also determine the evolution of the characteristic length scale, thus quantifying the impact of the external electric field on the coarsening of the defect network. / Neste trabalho estudamos numericamente a formação e dinâmica de defeitos topológicos em cristais líquidos nemáticos. Nosso estudo é baseado no modelo de Ginzburg- Landau, o qual descreve a evolução da ordem orientacional de um cristal líquido em termos de um tensor de segunda ordem simétrico e com traço nulo. Este modelo fenomenológico permite estudar a fase nemática em escalas que vão de poucos nanômetros até poucos micrômetros (escala mesoscópica). Para tal estudo numérico, desenvolvemos um programa de computador que denominamos de LICRA (Liquid CRystal Algotithm). Este programa combina o algoritmo de diferença finita para calcular derivadas espaciais com a integração temporal de Runge-Kutta para resolver a equação de relaxação da nematodinâmica, sem a presença de flutuações térmicas e fluxos hidrodinâmicos. Usando este programa de computador investigamos a dinâmica de coalescência em duas e três dimensões em um cristal líquido nemático uniaxial. Tanto o fator de estrutura quando a escala de comprimento característico foram calculadas no tempo. Espera-se que esta escala cresça como uma lei de potências do tempo, L ∝ tα, onde, a partir de uma análise dimensional, α = 1/2. Encontramos os valores de α = 0, 45 ± 0, 01 em duas dimensões e α = 0, 350 ± 0, 003 em três dimensões. Além disso, em todos os casos verificamos que a lei de Porod é satisfeita para número de ondas k de grandes valores. Utilizando LICRA, investigamos também a dinâmica de coalescência de cristais líquidos nemáticos em duas dimensões submetidos a um campo elétrico externo. Consideramos a anisotropia dielétrica positiva e negativa e duas diferentes possibilidades de orientação do campo elétrico: paralelo e perpendicular ao plano da rede bidimensional. Determinamos os efeitos de um pulso de campo elétrico na evolução da escala do comprimento característico e as alterações nas texturas dos cristais líquidos. Em particular, mostramos que os diferentes tipos de defeitos que são produzidos após o campo elétrico ser aplicado dependem da orientação do campo elétrico e do sinal da anisotropia dielétrica. Finalmente, apresentamos os efeitos da rotação de um campo elétrico externo na dinâmica de uma rede de defeitos semi-inteiros em cristais líquidos nemáticos em duas e três dimensões com anisotropia dielétrica negativa. Mostramos que, girando o campo elétrico por um ângulo π ao redor de um eixo pertencente a plano da rede, ocorre uma transformação contínua de todas as desclinações semi-inteiras da rede em desclinações com sinal oposto. Esta transformação é intermediada por desclinações do tipo torção. Além disso, determinamos a evolução da escala de comprimento característico quantificando o impacto do campo elétrico externo na dinâmica de coalescimento da rede.

Sintering, a process of forming dense solid bodies from powder compacts remains the most important route for processing of ceramics. The process of sintering involves formation and growth of necks during initial stage, coarsening, relative particle rotation, filling of connected pores in intermediate stage, filling of isolated pores during final stage sintering and rapid grain growth towards the end of densification. The processes involve a combi-nation of grain boundary diffusion, surface diffusion, grain boundary migration and grain boundary sliding. Studies of interfacial processes during sintering are still of interest since modifying interface structure offers a means to tailor low and high temperature mechanical properties of ceramics. Many of the studies in literature on single phase systems are based on geometric changes during sintering. Sintering has been modelled as 1D or 2D array of spheres. The simplest of these consist of a contacting pair of spherical particles. Early models studied changes in size and shape of the necks during initial stage sintering and associated mass transport mechanisms. There have been studies on coarsening that report shrinkage rates of smaller particles is a system of two particles with different radii. In both the cases of neck growth and coarsening, thermodynamic variables as given by dihedral angle (relative grain boundary to surface energy of the system) and kinetic parameters of grain boundary surface diffusivity have been found to influence the size and shape evolution with time. Also, there have been studies comparing self similar geometries at different absolute length scales such as a system of micro and nano sized particles, which show different sintering behaviour depending on the absolute particle size. There have been studies on multi particle arrays both linear and closed. Early studies on linear arrays observed rearrangement of particles and relative rotation due to non spherical shape and bond angle of an array of three particles. Also there was a study that predicted rearrangement due to differential shrinkage in an assembly containing a combi-nation of large and small particles. Similar observations were also made on closed arrays of four or more particles both in 2D and 3D. Formation of high energy local configurations such as six grain boundaries (GBs) meeting at a line were found, followed by the topological transitions such as formation of new GBs or elimination of existing ones, leading to specific features in sintering behaviour. Geometrical evolution during final stage sintering is critical for forming dense final products. While most studies related the shrinkage behaviour to shape of the pore (convex or concave) and the number of grains surrounding a pore, later the absolute size of the pore was observed to be an important parameter. In 2D simulations and experiments large convex pores were found to shrink due to mass transport from surrounding GBs. In 3D simulations, pores with large coordination number as high as 32, pore shrinkage was observed followed by gradual reduction in coordination number and final elimination. Also studied are evolution of pore -GB configuration in case of small pores as separation of these from GB and entrapment into grains will freeze further shrinkage. In addition to the geometry related changes are also crystallography related microstructural changes. Crystallographic arrangement at the atomic scale leads to anisotropy of interfacial energies and diffusivities, that effect microstructural evolution. The presence of positive and negative ions in ionic solids can result in additional features such as charged and neutral planes Crystallography can affect the rotation of powder particles in initial stage sintering to subtle differences in microstructure evolution during grain growth in final stage sintering. Conversely crystallography has to be related to diffusion at interfaces. The rotation of spheres is governed by energetics. The final configuration corresponds to local energy minima in misorientations between the spheres and the single crystal plate. This technique is useful in finding a number of crystallography related aspects such as low energy GBs and equilibrium shapes of metal droplets. Rotation of unconstrained crystal related to neighbouring crystal has also been observed in thin films. Surface energy anisotropy has often been studied using topography of annealed sur-faces studied using atomic force microscopy (AFM). While low energy stable surfaces show perfectly flat surfaces, planes close to a stable plane form terrace and ledge structures whereas unstable planes form hill and valley structures. A method of “inverse Wulff shape” of pores trapped in single crystals has been used to find relative stability of sur-face planes using a combination of electron back scattered diffraction (EBSD) and AFM. Crystallography is very much related to the phenomenon of abnormal grain growth that occurs during later stages of sintering. Similarly, polycrystal assemblies have shown varying GB migration velocities for different crystallographic planes. Most recently, 3D EBSD has been used to study crystallography of GBs in sintered polycrystalline materials. In the present study, we address two specific issues. The first is related to the effect of microstructure of polycrystalline powder particles on initial stage sintering, where we compare sintering between particles with same particle size but different grain sizes. The second is related to the crystallographic aspects of interfaces in sintered materials with specific reference to yttria stabilized cubic zirconia. The present study is mostly confined to pressure less (free) sintering where the only driving force is the reduction in interfacial energy of the system. The effect of polycrystalline nature on initial stage sintering is investigated and com-pared with the behaviour of single crystal particles. We extend the model by Coble on single crystals to polycrystalline particles containing space filling tetrakaidecahedral grains with an identical grain size. The grain boundaries within particles are considered to be additional sources for mass to be plated at the neck and the flux equations are suitably modified. A model was developed to characterize the variation with time in the growth rate (x/R), where x and R are radii of the neck and particle respectively. The model indicated that the neck growth rate for polycrystalline spheres was faster compared to single crystals towards end of initial stage sintering (large value of x/R). There is large scope for extending the model further for complex geometries, diffusion distances and grain size distributions. Sintering experiments were conducted with annealed 2D random arrays of spheres of zirconia with two different grain sizes and a particle size of 40 m. Two different forms of zirconia (8YCZ and 3YTZ) were used as model systems for a few and a large number of grains in a particle respectively. The experimental results were limited, but broadly consistent with the new model. However necks were found to grow to a value f x=R = 0:12 and they did not grow further. In the second part of our study, grain boundaries in yttria stabilized cubic zirconia were studied in the context of macroscopic crystallographic parameters of misorientations of grains on either side of the grain boundary and crystallographic coordinates of grain boundary planes. Our aim was to study the evolution of misorientations and grain bound-ary planes during sintering process, starting from formation of necks during the initial stage to grain boundary migration during later stages. Orientation imaging microscopy based on an EBSD technique in an SEM was carried out on fully dense samples and also on porous samples obtained by interrupting sintering before attaining full density. The fraction of CSL misorientations on nearly dense cubic zirconia with grain sizes varying from submicrocrystalline 0.61 to 10 m was close to a random distribution. The number fraction of necks with CSLs formed in porous cubic zirconia with microcrysatlline particles was slightly higher than a random distribution. However, the present study covers only nearly dense-microcrystalline, nearly dense- submicrocrystalline, porous - microcrystalline regime , but misorientation information could not be obtained experimentally in a low density - submi-crocrystalline regime that is critical for sintering process. We also studied the distribution of grain boundary planes in fully dense 8YCZ with a grain size of 2.8 m by a stereological method using 2D OIM data. The overall distribution of grain boundary planes showed very weak anisotropy with slight maxima with 1.1 multiples of random distribution (MRD) at {100} planes, which is consistent with observations in literature on larger grain sizes. Interestingly, the planes that were abundant were not low energy surface planes (also mentioned in literature), in clear contrast with other ceramics studied in literature. The distribution of grain boundary planes was also plotted for specific misorientations, including those around low index axes of [100], [110], [111] and low misorientations. The grain boundary character distribution (GBCD) shows a high frequency of occurrence in position of pure twists about [100] and symmetric tilts at certain low misorientations . The highest frequency of occurrence was observed for coherent twin 3 on {111} plane and symmetric tilt (higher order twin) 11 on {113} plane, both corresponding to low energy GBs reported in literature in bicrystal experiments. With pure twists on {100} for rotations about [100] axis and pure tilts with {11w} or {1ww} planes for rotations about [110], both the criteria for specialness based on surface planes forming GB or symmetric tilts are found to be valid for specific cases. Notable is the frequency of occurrence of coherent twin 3 on {111} and 11 on {113}, that was 4.8 MRD for microcrystalline 8YCZ and as high as 7.8 MRD for submicrocrystalline 8YCZ samples, which is much higher than frequency of occurrence of any GB plane in any oxide studied in literature.

Automotive industry products portfolio includes a wide variety of complex‐shaped cast iron products, such as truck engine components, that need to withstand a constant trend of higher demands, especially urged by stricter environmental regulations on emissions. Combined with this continued demand on properties improvement, cast iron industry faces a process problem related to the lack of understanding of solidification and mechanisms behind defect formation. Casting products are highly affected by the product design and the manufacturing method itself, which governs the final microstructure and hence the final mechanical properties. Wall thickness of the moulding material strongly influences the solidification time, varying the microstructural coarseness, resulting in a component with different properties depending on the local shape of the casting. The main objective of this work is the characterization of the primary austenite microstructure and its coarsening process, which has been poorly documented in cast iron literature, to allow the prediction and control of these microstructural features present in the casting. The microstructural evolution of the primary austenite in hypoeutectic lamellar graphite iron (LGI) is studied under isothermal coarsening conditions. The dendritic microstructure suffered major morphological changes that included dendrite fragmentation, globularization, and coalescence. Empirical relations based on morphological parameters are introduced to predict the microstructural evolution of primary austenite. A novel technique for colour‐etching and semi‐automatic image analysis for the characterization of quenched dendritic microstructures in cast iron is presented. A new experimental technique for production of graphitic iron with varying nodularity is presented as a solution to control the production of compacted (CGI) and spheroidal graphite iron (SGI) under laboratory conditions. The nodularity evolution is controlled as a function of the holding time and the residual Mg, allowing the study of the primary solidification and primary microstructures of hypoeutectic CGI and SGI in future investigations.

Les exigences des clients du secteur aéronautique imposent aux entreprises de prendre en compte pour le dimensionnement les effets de la température sur toute la durée de vie du produit. Cependant, aucune loi ne permet actuellement de prévoir l’impact du vieillissement thermique sur le comportement des matériaux. Ce travail a pour objectif de comprendre le mécanisme de vieillissement thermique des alliages d’aluminium et son impact sur les propriétés mécaniques, mais surtout d’acquérir un outil performant capable d’obtenir rapidement des données matériaux après vieillissement.Au cours de cette étude, de nombreuses analyses microstructurales et mécaniques ont été réalisées sur trois alliages d’aluminium à durcissement structural. Différentes combinaisons temps-température de vieillissement ont été testées afin de disposer d’une large base de données sur ces matériaux (caractéristiques mécaniques statiques Rm, Rp0,2 et dureté et tailles des précipités durcissants). Ces données ont ensuite été compilées dans un modèle de vieillissement basé sur les théories classiques de durcissement structural, de croissance et de coalescence des précipités.Le modèle de vieillissement créé répond au besoin initial et prédit de façon conservative le comportement mécanique des alliages ayant subi un vieillissement thermique isotherme. Des axes d’amélioration sont envisagés pour ce modèle évolutif, comme l’intégration de la prévision du comportement en fatigue ainsi que le traitement de cas anisothermes pour une représentation plus réelle des conditions de service des pièces aéronautiques. / In aeronautics, customers ask companies to consider the effects of temperature over the entire life of the product in structural requirements. Indeed, aircraft parts are demanded to last longer (up to 90 000 hours) and operate at higher temperatures (up to 250°C). No laws enable to predict the impact of thermal ageing on materials behavior. Current practices are to perform mechanical testing after ageing in ovens at various temperatures, but they are expensive and incompatible with the development schedules. This work aims to understand the thermal aging mechanism of aluminum alloys and its impact on mechanical properties, but especially to acquire a powerful tool able to quickly obtain material data after aging.During this study, many microstructural and mechanical analyses were conducted on three precipitation hardened aluminum alloys. Different combinations of aging time and temperature were tested to get a large database of these materials (static mechanical characteristics Rm, Rp0,2 and hardness and sizes of hardening precipitates). These data were then compiled into a computing aging model based on the classical theories of precipitation hardening, growth and coarsening of precipitates.The created aging model responds to the initial need and can conservatively predict the mechanical behavior of aluminum alloys under isothermal aging. Improvement areas are considered for this evolutionary model, such as the integration of fatigue behavior prediction and the inclusion of thermal cycles for a more realistic representation of service conditions of aircraft parts.

The aim of this work was to systematically study how the microstructure evolution is affected by the carbon activity in WC-Ni cemented carbides. Seven WC-9.59at%Ni alloys with different carbon activity were sintered at 1500 °C. From investigating these alloys, the carbon window has been experimentally evaluated using light optical microscopy and compared to theoretical carbon window calculated using Thermo-Calc. The overall microstructure of cross sections and raw surfaces have been investigated using scanning electron microscopy. Finally, the WC grain size and distribution have been evaluated using electron backscatter diffraction. It was found that the experimental carbon window was slightly wider than the theoretical carbon window. The WC grain size increased and the grain size distribution got wider with increasing carbon activity. In addition, the largest WC grains showed the largest grain growth by increasing carbon activity. By comparing the present results of grain size and distribution of WC-Ni to previous results of WC-Co, it was found that the WC grain growth was more pronounced and more influenced by the carbon activity.