O presente trabalho apresenta um estudo sobre o amolecimento após laminação e recozimento da AA 7075, uma liga de alumínio endurecível por precipitação . As amostras recebidas no estado T6 foram caracterizadas com auxílio das técnicas de microscopia óptica de luz polarizada, microscopia eletrônica de varredura, espectroscopia de raios X por dispersão de energia, difração de raios X, condutividade elétrica e dureza Vickers . As amostras foram então separadas em dois grupos. O primeiro sofreu um tratamento térmico de solubilização (485°C por 5 horas) enquanto o segundo foi submetido a um tratamento de superenvelhecimento (300°C por 5 horas) e, em seguida, ambos os grupos de amostras tratadas foram novamente caracterizadas pelas técnicas descritas anteriormente (exceto microscopia óptica) e laminadas a frio. Durante a etapa de laminação, constatou-se a dificuldade em causar deformação plástica na amostra solubilizada. Optou-se em conduzir o estudo com as amostras superenvelhecidas, que foram laminadas com reduções de 45%, 75% e 90% em espessura. A seguir, estas foram submetidas a tratamentos isotérmicos e isócronos com o objetivo de estudar a cinética de amolecimento das amostras deformadas a frio. As amostras superenvelhecidas e deformadas em 45% em redução de espessura, apresentaram somente indícios de início de recristalização (nas amostras tratadas a partir de 250°C por 1 hora) via EBSD, sendo que a maior parte do amolecimento pode ser explicada pelo mecanismo de recuperação. Além disso, a cinética de amolecimento das amostras recozidas nesse grupo apresentaram boa concordância com a lei logarítmica proposta por Kulhmann (1948) e (coincidentemente) também com o consolidado modelo JMAK. As amostras superenvelhecidas e deformadas em 75% e 90% apresentaram comportamento similar (isso é, principalmente recuperação) para recozimentos realizados em temperaturas de até 350°C por uma hora. Recozimentos realizados a 400°C promoveram a recristalização total das amostras desse grupo para tempos inferiores a 15 minutos. Dessa forma, não foi possível estudar a cinética de recristalização para esse segundo grupo de amostras. / This work presents a study about the softening after cold rolling and annealing of aluminium alloy AA 7075. Firstly, polarized light optical microscopy, scanning electron microscopy, energy dispersive X-ray spectroscopy, X-ray diffraction, electrical conductivity and Vickers hardness have been used at the starting material (T6). The samples were then separated in two groups. The former underwent a solubilization heat treatment (485°C for 5 hours) whilst the latter underwent an overaging treatment to grow up the existing precipitates (300°C for 5 hours). Both groups of treated samples were again characterized by the techniques described above (except optical microscopy). In the rolling stage, the difficulty in straining the solubilized sample and the relative ease for doing so to the overaged sample was verified. It was therefore decided to conduct the study with the samples of the second group, which were 45%, 75% and 90% rolled in thickness reduction. Then, they underwent isothermal and isochronous treatments in order to study its softening kinetics by Vickers hardness measurements, polarized light optic microscopy and EBSD. The overaged and rolled samples (45% in thickness reduction) didn\'t present evidences of recrystallization except by very few grains found via EBSD (in samples treated from 250 ° C for 1 hour). So, most of the observed softening can be explained by recovery. In addition, the softening kinetics of the annealed samples in this group showed good agreement with the logarithmic law proposed by Kulhmann (1948) and (coincidentally) also with the consolidated JMAK model. The overaged samples that underwent thickness reduction of 75% and 90% showed a similar behavior (that is, mainly recovery) for annealing at temperatures up to 350 ° C. Annealing at 400 ° C promoted total recrystallization of the samples from this group (75% and 90% in thickness reduction) in less than 15 minutes. Thus, it was not possible to study the kinetics of recrystallization for this second group of samples.

O presente trabalho apresenta um estudo sobre o amolecimento após laminação e recozimento da AA 7075, uma liga de alumínio endurecível por precipitação . As amostras recebidas no estado T6 foram caracterizadas com auxílio das técnicas de microscopia óptica de luz polarizada, microscopia eletrônica de varredura, espectroscopia de raios X por dispersão de energia, difração de raios X, condutividade elétrica e dureza Vickers . As amostras foram então separadas em dois grupos. O primeiro sofreu um tratamento térmico de solubilização (485°C por 5 horas) enquanto o segundo foi submetido a um tratamento de superenvelhecimento (300°C por 5 horas) e, em seguida, ambos os grupos de amostras tratadas foram novamente caracterizadas pelas técnicas descritas anteriormente (exceto microscopia óptica) e laminadas a frio. Durante a etapa de laminação, constatou-se a dificuldade em causar deformação plástica na amostra solubilizada. Optou-se em conduzir o estudo com as amostras superenvelhecidas, que foram laminadas com reduções de 45%, 75% e 90% em espessura. A seguir, estas foram submetidas a tratamentos isotérmicos e isócronos com o objetivo de estudar a cinética de amolecimento das amostras deformadas a frio. As amostras superenvelhecidas e deformadas em 45% em redução de espessura, apresentaram somente indícios de início de recristalização (nas amostras tratadas a partir de 250°C por 1 hora) via EBSD, sendo que a maior parte do amolecimento pode ser explicada pelo mecanismo de recuperação. Além disso, a cinética de amolecimento das amostras recozidas nesse grupo apresentaram boa concordância com a lei logarítmica proposta por Kulhmann (1948) e (coincidentemente) também com o consolidado modelo JMAK. As amostras superenvelhecidas e deformadas em 75% e 90% apresentaram comportamento similar (isso é, principalmente recuperação) para recozimentos realizados em temperaturas de até 350°C por uma hora. Recozimentos realizados a 400°C promoveram a recristalização total das amostras desse grupo para tempos inferiores a 15 minutos. Dessa forma, não foi possível estudar a cinética de recristalização para esse segundo grupo de amostras. / This work presents a study about the softening after cold rolling and annealing of aluminium alloy AA 7075. Firstly, polarized light optical microscopy, scanning electron microscopy, energy dispersive X-ray spectroscopy, X-ray diffraction, electrical conductivity and Vickers hardness have been used at the starting material (T6). The samples were then separated in two groups. The former underwent a solubilization heat treatment (485°C for 5 hours) whilst the latter underwent an overaging treatment to grow up the existing precipitates (300°C for 5 hours). Both groups of treated samples were again characterized by the techniques described above (except optical microscopy). In the rolling stage, the difficulty in straining the solubilized sample and the relative ease for doing so to the overaged sample was verified. It was therefore decided to conduct the study with the samples of the second group, which were 45%, 75% and 90% rolled in thickness reduction. Then, they underwent isothermal and isochronous treatments in order to study its softening kinetics by Vickers hardness measurements, polarized light optic microscopy and EBSD. The overaged and rolled samples (45% in thickness reduction) didn\'t present evidences of recrystallization except by very few grains found via EBSD (in samples treated from 250 ° C for 1 hour). So, most of the observed softening can be explained by recovery. In addition, the softening kinetics of the annealed samples in this group showed good agreement with the logarithmic law proposed by Kulhmann (1948) and (coincidentally) also with the consolidated JMAK model. The overaged samples that underwent thickness reduction of 75% and 90% showed a similar behavior (that is, mainly recovery) for annealing at temperatures up to 350 ° C. Annealing at 400 ° C promoted total recrystallization of the samples from this group (75% and 90% in thickness reduction) in less than 15 minutes. Thus, it was not possible to study the kinetics of recrystallization for this second group of samples.

High strength 7xxx aluminium alloys are used extensively in the aerospace industry because the alloys offer excellent mechanical properties. Unfortunately, the alloys can suffer localised corrosion due to the presence of large intermetallic particles at the alloy surface that are aligned in the rolling direction. Laser surface melting (LSM) techniques offer the potential to reduce and/or to eliminate the intermetallic phases from the surface of the alloy without affecting the alloy matrix.The present study concerns the application of LSM using an excimer laser to enhance the corrosion resistance of AA 7075-T6 aluminium alloy. The initial stage of the project was aimed at optimising the laser conditions for production of a uniform microstructure, with the increase in the corrosion resistance of the alloy being determined by potentiodynamic polarization measurements in sodium chloride solution. Low and high laser energy densities were used with a different number of pulses per unit area to treat the alloy surface, which were achieved by changing both the laser fluence and the pulse repetition frequency. A laser fluence of 3.3 J/cm2 with 80 pulses was subsequently selected as the optimum condition to treat the surface of the alloy. The composition and microstructure of the alloy before and after LSM treatment, and following corrosion tests, were characterized by scanning electron microscopy (SEM), transmission electron microscopy (TEM) and X-ray diffraction (XRD).After the laser treatment, the surface and the cross-sections of the alloy showed a significant reduction in the number of large intermetallic particles and a relatively homogenous melted layer was generated that provided significant improvement in the resistance of the alloy against corrosion, as assessed by several corrosion test methods, including exfoliation corrosion (EXCO) tests. However, delamination of the melted layer was observed after extended testing in the EXCO solution which is possibly related to the formation of bands of fine magnesium and zinc-rich precipitates within the melted layer. Therefore, anodising in sulphuric acid was applied to the LSM alloy, in order to further increase the corrosion resistance and to protect the laser treated layer from delamination by generating a thin oxide film over the LSM layer. The results revealed that the anodic treatment increased the resistance of the alloy to exfoliation attack.

Submitted by Luiza Maria Pereira de Oliveira (luiza.oliveira@ufpe.br) on 2017-07-14T14:18:45Z No. of bitstreams: 2 license_rdf: 811 bytes, checksum: e39d27027a6cc9cb039ad269a5db8e34 (MD5) TESE Heronilton Lira.pdf: 8484654 bytes, checksum: 5dca5cb2c7da509efe20982091cee6db (MD5) / Made available in DSpace on 2017-07-14T14:18:45Z (GMT). No. of bitstreams: 2 license_rdf: 811 bytes, checksum: e39d27027a6cc9cb039ad269a5db8e34 (MD5) TESE Heronilton Lira.pdf: 8484654 bytes, checksum: 5dca5cb2c7da509efe20982091cee6db (MD5) Previous issue date: 2016-07-01 / O desenvolvimeto de compósitos a base da liga de alumínio AA 7075 com reforço nanoparticulado de 2% SiC, 2% TiN e 2% ZnO foi realizado através da moagem de alta energia em banho de álcool e extrusão a quente. Neste estudo, os pós recebidos e processados foram analisados por difração de raios X (DRX), difração de laser (DL), microscopia eletrônica de varredura (MEV) e espectrometria por energia dispersiva de raios X (EDS).Após a extrusão, as amostras foram caracterizadas por difração de raios X (DRX),microscopia eletrônica por varredura (MEV), espectrometria por energia dispersiva de raios X (EDS), dureza vickers e pelo ensaio de desgaste por abrasão via pino sobre disco. Os pós compósitos produzidos apresentaram os reforços incorporados a matriz e sem alterar significativamente o tamanho do cristalito, distribuição ou morfologia das partículas. As extrusões apresentaram grãos heterogêneos achatados e deformados na direção do processo. Os principais fatores que influenciaram os resultados das amostras após extrusão foram o tamanho do cristalito e a microestrutura obtida devido a natureza do reforço usado. Materiais de menores tamanhos de cristalito e de estrutura mais homogênea resultaram em materiais mais resistentes a dureza e consequentemente ao desgaste. O melhor resultado foi encontrado para o compósito AA 7075-2% TiN. / The development of composites aluminum alloy AA 7075 reinforced with 2% SiC, 2% TiN and 2% ZnO nanoparticulates was performed by High Energy Ball Milling in a bath of alcohol and hot extrusion. In this work, the powders received and processed were analyzed by X ray diffraction (XRD), laser diffraction (LD), scanning electron microscopy (SEM) and energy dispersive X rays spectrometry (EDS). After extrusion, the samples were characterized by X rays diffraction (XRD), scanning electron microscopy (SEM), energy dispersive X rays spectrometry (EDS), vickers hardness and the test abrasive wear via pin on disc. The composites powders showed the reinforcements incorporated into the matrix and no change of crystallite size, particle size distribution or morphology. The extrusions presented heterogeneous grains deformed and flattened in the direction of process. The main factors that influenced the results of specimens after extrusion were the crystallite size and the microstructure obtained due to the nature of reinforcement used. Materials of smaller crystallite sizes and homogeneous structure resulted in stronger materials to the hardness and abrasive wear. The best result was found for the composite AA 7075-2%TiN.

A Lagrangian finite-element model of the plunge phase of the friction stir welding process was developed to better understand the plunge. The effects of both modeling and experimental parameters were explored. Experimental friction stir plunges were made in AA 7075-T6 at a plunge rate of 0.724 mm/s with spindle speeds ranging from 400 to 800 rpm. Comparable plunges were modeled in Forge2005. Various simulation parameters were explored to assess the effect on temperature prediction. These included the heat transfer coefficient between the tool and workpiece (from 0 to 2000 W/m-K), mesh size (node counts from 1,200 to 8,000), and material model (five different constitutive relationships). Simulated and measured workpiece temperatures were compared to evaluate model quality. As spindle speed increases, there is a statistically significant increase in measured temperature. However, over the range of spindle speeds studied, this difference is only about 10% of the measured temperature increase. Both the model and the simulation show a similar influence of spindle speed on temperature. The tool-workpiece heat transfer coefficient has a minor influence (<25% temperature change) on simulated peak temperature. Mesh size has a moderate influence (<40% temperature change) on simulated peak temperature, but a mesh size of 3000 nodes is sufficient. The material model has a high influence (>60% temperature change) on simulated peak temperature. Overall, the simulated temperature rise error was reduced from 300% to 50%. It is believed that this can be best improved in the future by developing improved material models.