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, Étude de la séquence de précipitation pendant une isotherme à 100°C : influence de la déformation

, L'évolution des zones-GP (0-3 nm) est étudiée grâce aux graphiques (a, c, e) de la Figure 5. 17. Après 1h de traitement à 100°C, une fraction volumique similaire des zones-GP, pp.0-3

, Après 10h et jusqu'à 48h à 100°C, la distribution de taille des zones-GP s'élargit et le rayon moyen

, Les échantillons déformés par HPS (? ? 15, ? ? 20 et ? ? 30) ont également été étudiés en SAXS pendant une isotherme à 100°C, ainsi que les échantillons 0,4% SC déformé à ? ? 2000 et 0,8% FC après mise en solution

, i)) montrent que, comme pour l'alliage déformé par HPT, la taille de grains semble rester stable lors du traitement à 70°C quel que soit le taux de déformation. Les cartographies KAM (Figure 5. 28) montrent que les désorientations inférieures à 10° n'évoluent pas lors du recuit à 70°C, se traduisant par des densités de dislocations (désorientations) suivantes : de 2,67±0,39.10 15 m -2 à 1,96±0,04.10 15 m -2 pour l'alliage déformé à ? ? 15

, Les cartographies ASTAR de l'alliage 0,4% SC déformé par HPS avec ? ? 15 puis recuit à 70°C ou 100°C (Figure 5. 28 (a, c, e)) montrent que la taille de grains ne croit pas de façon importante après les recuits

, 28 (b, d, f)) montrent qu'un recuit plus intense entraine la formation de désorientations intragranulaire regroupées sous forme de sous-joints de grains (désorientations moins diffuses dans les grains, Les densités de dislocations calculées diminuent peu après un recuit à 70°C (de 2,67±0,39.10 15 m -2 après déformation à 1,96±0,04.10 15 m -2 ), vol.5

, Les images STEM DF et HAADF (Figure 5. 30 et Figure 5. 31) montrent qu'après 72h à 70°C la nanostructure des alliages déformés par HPS, quel que soit le taux déformation, présente une forte densité de précipités. On retrouve, comme indiqué par les résultats SAXS

, Après un traitement à 100°C, pour l'alliage déformé avec ? ? 15 (Figure 5. 30), une évolution très hétérogène des précipités est observée. Cette hétérogénéité, déjà remarqué à 70°C, est accentuée après un recuit à 100°C comme le montrent les images HAADF (Figure 5. 30(h, i)) : la microstructure est découpée en plusieurs zones, celles qui semblent contenir des petits grains, et où la précipitation est donc principalement intergranulaire

, De plus, à l'intérieur même de ces zones intra-granulaires, il semble que la distribution de taille des précipités soit très large

, Cette hétérogénéité dans la précipitation n'est pas retrouvée dans les images STEM de l'alliage déformé

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É. À-cette, le seul point négatif est le taux de déformation nécessaire pour obtenir ces résultats, en effet, étant très élevé, il est difficile d'imaginer une transposition de cette stratégie à grande échelle

, Néanmoins, ces résultats nous ont permis de poursuivre le projet par la deuxième étape qui consiste à

, la déformation intense sur l'alliage 0,4% SC avait pour but d'affiner la taille de grains mais également de fragmenter les particules intermétalliques afin d'obtenir une stabilité thermique élevée comme pour l'alliage modèle Al-Fe. Après ? ? 15, 20, 30 par HPS et ? ? 200 et 2000 par HPT, la taille de grains est affinée (<500nm) et le phénomène de saturation de la taille de grains (observé pour l'alliage modèle Al-Fe)

, le même temps, l'influence de la solidification rapide, qui devait permettre d'obtenir une densité numérique élevée d'intermétalliques, n'a également pas permis de favoriser la fragmentation. Malgré tout, l'étude des microstructures a montré qu'en plus des grains ultrafins, de nombreuses désorientations intra-granulaires

, Cette seconde étape a permis de montrer que dans les alliages 7###, la phase Al7Cu2Fe formée ne se fragmente pas autant que la phase Al6Fe de l'alliage Al-Fe, des facteurs tels que la forme, la taille et la fraction volumique des particules en sont probablement des raisons. Néanmoins, la résistance de l'alliage est largement augmentée principalement grâce à la taille de grains et aux nombreuses désorientations intra-granulaires créé par la déformation, De plus les ségrégations et la précipitation sur les défauts ont également été révélées

, Ainsi, la dernière étape de l'étude a consisté en l'étude de la stabilité thermique des alliages déformés ainsi que l'influence de la déformation sur la séquence de précipitation. Et finalement

, Dans un premier temps, un recuit à 70°C pendant 72h a engendré une recristallisation, sauf pour

, par la précipitation intergranulaire, qui donne des précipités plus gros que lors du précédent recuit. Cette intense précipitation Figure C. 2:Taille de grains en fonction de la limite d'élasticité pour l'alliage 0,4% SC non-déformé, déformé à différents taux et recuit à différentes températures. 'éléments d'alliages, et peut être faire un simple alliage Al-Zn-Mg, avec des pourcentages poids faibles et ainsi étudier si ces quantités permettent d'obtenir un alliage à grains ultrafins et si les précipités sont suffisants pour stabiliser cette microstructure. Y aurait-il encore des précipités intra-granulaires ? Si non, cela engendrerai-t-il une perte importante de résistance ? Il serait également intéressant de pousser l, Dans un second temps, un recuit à 100°C pendant 48h a engendré un régime de croissance pour l'alliage stabilité est également apportée, lors de ce recuit

. Comme-le-mn and . Le-cr, Enfin une dernière perspective pourrait être de pousser l'idée des particules intermétalliques mais en utilisant d'autres éléments que le fer

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