http://purl.fcla.edu/fcla/etd/CFE0003747

Thesis (Ph.D.)--McMaster University (Canada), 1995. / Source: Dissertation Abstracts International, Volume: 57-03, Section: B, page: 1872. Adviser: B. D. Gaulin.

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Made available in DSpace on 2014-10-09T12:53:58Z (GMT). No. of bitstreams: 0 / Made available in DSpace on 2014-10-09T14:09:28Z (GMT). No. of bitstreams: 0 / Este trabalho tem como objetivo o desenvolvimento de um combustível nuclear de alta densidade e baixo enriquecimento com base na liga ?-UMo, para aplicações nas quais seja necessário desempenho satisfatório a altas temperaturas, considerando-se a sua utilização na forma de dispersão. Para tanto, partiu-se da análise dos resultados dos testes RERTR (sigla em inglês para \"Reduced Enrichment of Research and Test Reactors\") e de alguns trabalhos teóricos envolvendo a elaboração de ligas metaestáveis de ?-urânio. Uma adição ternária é proposta, com base em propriedades de ligas binárias e ternárias de urânio-molibdênio estudadas, e que teve como objetivos um aumento na estabilidade da fase gama do urânio e a facilidade na obtenção dos pós. Assim, as ligas de urânio-molibdênio foram preparadas com adições de Mo de 5 a 10% em peso, e adição de 1 e 3% de elemento ternário (o silício), sobre uma liga base binária de U7Mo. Em todas as fases do processo de preparação, as ligas foram caracterizadas pelas técnicas tradicionais, para determinação de suas propriedades estruturais e mecânicas. Para a elaboração de um processo para a obtenção de pós destas ligas, o seu comportamento sob atmosfera de hidrogênio foi estudado em equipamento de análise térmica e gravimétrica diferencial. Temperaturas variaram da ambiente a 1000oC, por tempos de 15 minutos a 16 horas. A validação destes resultados foi feita em escala semi-piloto, na qual quantidades de 10 a 50g de pós de algumas das ligas foram preparados, sob atmosfera estática de hidrogênio. Os estudos de compatibilidade foram conduzidos expondo-se as ligas à atmosfera de oxigênio e ao contato com alumínio, para a verificação de possíveis reações por meio de análise térmica diferencial. As ligas foram submetidas a aquecimento constante até temperatura de 1000oC, e seu desempenho foi avaliado quanto a maior resistência à reação. 6 Com base nestes resultados, observou-se que as adições ternárias aumentam as temperaturas para a oxidação das ligas e reação com alumínio frente aos binários ?UMo. Um conjunto de condições para hidretação das ligas e fabricação dos pós foi estabelecido, tanto mais restritivos em termos de tempo, temperatura e necessidade de pré-tratamentos quanto mais estável a estrutura ?. Com a adição de ternário em pequeno excesso e formação de fase intergranular, mostrou-se que um aumento na estabilidade não prejudica a formação dos pós. / Tese (Doutoramento) / IPEN/T / Instituto de Pesquisas Energéticas e Nucleares - IPEN-CNEN/SP

Energy needs are projected to continue to increase in the coming decades, and with the drive to use more clean energy to combat climate change, nuclear energy is poised to become an important player in the energy portfolio of the world. Due to the unique nature of nuclear energy, it is always vital to have safe and efficient generation of that energy. In current light water reactors, the most common fuel is uranium dioxide (UO2), an oxide ceramic. There is also ongoing research examining uranium-based based metallic fuels, such as uranium-molybdenum (U-Mo) fuels with low uranium (U) enrichment for research reactors as part of a broader effort to combat nuclear proliferation, and uranium-zirconium-based fuels for Generation IV fast reactors. Each nuclear fuel has weaknesses that need to be addressed for safer and more efficient use. Two major challenges of using UO¬2 are the fission gas (e.g. xenon) release and the decreasing thermal conductivity with increasing burnup. In UMo alloys, the major weakness is the breakaway swelling that occurs at high fission densities. The challenges presented by both fuel types are heavily impacted by microstructure, and several studies have identified that the initial microstructure of the fuel in particular (e.g. initial grain size and grain aspect ratio) plays a large role in determining when and how quickly these processes occur. Thus, knowledge of how such initial microstructures evolve is paramount in having stable and predictable fission gas release and thermal conductivity decrease (in UO2) and fuel swelling (in UMo alloys). Mobility is a critical grain boundary (GB) property that impacts microstructural evolution. Existing literature examines GB mobility for a few specific boundaries but does not (in general) identify the anisotropy relationships that this property has. This work first examined the anisotropy in GB mobility, specifically identifying the anisotropy trend for the low-index rotation axes for tilt GBs in BCC γ U, and fluorite UO2 via molecular dynamics simulation. GB mobility is calculated using the shrinking cylindrical grain method, which uses the capillary effect induced by the GB curvature to drive grain growth. The mobilities are calculated for different rotation axes, misorientation angles, and temperatures in these systems. The results indicated that the density of the atomic plane perpendicular to the (tilt) GB plane (which is also perpendicular to the rotation axis) significantly impacts which GB rotation axis has the fastest boundaries. Specifically, the atomic plane that has a higher density tends to have a faster mobility, because it is more efficient for atoms moving across the GB along such planes. For example, for body-centered cubic materials, the <110> tilt GBs are determined to have the fastest mobilities, while face-centered cubic (FCC) and FCC-like structures such as fluorite have <111> tilt GBs as the fastest. Knowledge of GB mobility and its anisotropy in pure materials is helpful as a baseline, but real materials have solutes or impurities (both intentionally and unintentionally) which are known to affect GB mobility by processes such as solute drag and Zener pinning. Additionally, in reactors, nuclear fission can produce many fission products, each of which acts as an additional impurity that will interact with the GB in some way. Because the initial microstructure and its subsequent evolution are vital for addressing the challenges of using nuclear fuel as described above, knowledge of the impacts of these impurities on GB mobility is required. Therefore, this work examined the impact of solutes and impurities on GB mobility and its anisotropy. In particular, the solute effect was examined using the UMo alloy system, while the impurity effect was examined using Xe (a very common fission product) in the γ U, UMo, and UO2 systems. It is found that both Mo and Xe can cause a solute drag effect on GB mobility in the γ U system, with the effect of Xe being stronger than Mo at the same solute/impurity concentration. Xe also causes a solute drag effect in UO2, though the magnitude of the effect is interatomic-potential-dependent. The mobility anisotropy trend was found to disappear at high solute and impurity concentrations in the metallic U and UMo systems but was largely unaffected in the UO2 system. These results not only increase our fundamental understanding of GB mobility, its anisotropy, and solute/impurity drag effects, but also can be used as inputs for mesoscale simulations to examine polycrystalline grain growth with anisotropic GB mobility and in turn examine how the fuel performance parameters change with these properties. / Doctor of Philosophy / Worldwide, energy needs continue to increase each year. Concerns related to climate change have led to an increased emphasis on renewable energies such as solar and wind, but the limitations of these resources prevent them from being the only energy sources. Nuclear energy is uniquely positioned to address several energy concerns: it is clean (no carbon emissions and air pollution), reliable (for example, 24/7 energy production, independent of weather), and energy-dense (one kilogram of fissile uranium provides roughly the same amount of energy as 3000 metric tons of coal). Currently, nuclear energy provides roughly 20% of the energy of the United States, but future predictions show a decrease in the total share of energy generation due to aging systems and a limited number of new reactors being built. The safety and efficacy of existing and future reactors are among the primary concerns for being able to allow nuclear energy to increase its energy share. To determine the safety and efficacy of new reactor designs, a computer simulation tool called fuel performance modeling has been used over the last few decades. This tool requires several material properties as input, one of which is how the nuclear reactor fuel microstructure changes based on a variety of conditions. A significant process contributing to microstructural change is grain growth. Grains (crystallites that make up the whole material) meet at interfaces called grain boundaries (GBs), and these GBs have two properties that largely determine how grain growth occurs: energy and mobility. Significant effort is being put into understanding these properties and their anisotropy, or how they change based on the GB character which is the relative mismatch between the two grains. This work contributes additional understanding of GB mobility anisotropy in two nuclear fuels: uranium dioxide (UO2, the primary fuel in current reactors) and a uranium-molybdenum (UMo) alloy (the primary fuel for newer research reactors). In particular, computer simulation is used to determine GB mobility for several unique GB systems. It is found that for pure nuclear fuels, GB mobility anisotropy is largely determined by which atomic plane has the highest density perpendicular to the GB. When the fuel is no longer pure (through the addition of alloying elements or other impurities) the anisotropy changes significantly in UMo fuels, such that at high concentrations of solute or impurities there is little to no anisotropy, while very little change is observed in the anisotropy in UO2.

Coordenação de Aperfeiçoamento de Pessoal de Nível Superior / Neste trabalho foram realizadas a cominuição e passivação da liga metálica U-4Zr-2Nb pelo processo de hidretação-desidretação, bem como o estudo da sua cinética. A obtenção deste material pulverizado através das técnicas da metalurgia do pó é uma etapa necessária e chave na fabricação da pastilha, que será empregada na laminação da placa combustível. Foi escolhida a liga com composição U-4Zr-2Nb devido à sua elevada densidade e baixo teor de elementos de liga, além de suas pequenas seções de choque para nêutrons térmicos. Previamente, foi projetado e construído o equipamento tipo Sievert volumétrico para a cominuição da liga metálica de urânio pelo processo de hidretação-desidretação, operacionalizando-o no modo automático, através da aquisição de dados por intermédio de softwares também desenvolvidos neste trabalho. Juntamente com o desenvolvimento deste equipamento, outro software foi desenvolvido para calcular a cinética de hidretração e a porcentagem hidretada. A seguir, com a utilização deste equipamento, amostras da liga U-4Zr-2Nb foram tratadas termicamente, hidretadas, passivadas, moídas e desidretadas. O processo de cominuição desenvolvido foi realizado nas condições de temperaturas de hidretação variando entre 108C e 295C e a pressão variando entre 2,0 bar e 1,5 bar. Todas as amostras foram hidretadas por completo, independentemente da temperatura de processamento. O tempo de hidretação variou entre 550 a 16176 segundos, de acordo com a temperatura utilizada, sendo mais rápido para temperaturas mais altas. Independentemente dos tratamentos térmicos feitos previamente nas amostras, todas apresentaram somente a fase &#945; e, conseqüentemente, todas as hidretações realizadas foram massivas. Foi desenvolvido também um processo de passivação dos pós obtidos, tendo-se conseguido amostras cominuídas estáveis, ou seja, não apresentaram reações pirofóricas quando expostas ao ar, nem uma excessiva oxidação das mesmas. Para isto, foi utilizada uma mistura de gases contendo 90% de argônio e 10% de oxigênio. Após a passivação, os hidretos foram moídos e passivados novamente para obtenção final do pó metálico. A granulometria final dos pós metálicos obtidos não depende dos tratamentos térmicos da amostra nem da temperatura de hidretação. As partículas maiores se revelaram um aglomerado de partículas menores e, portanto, foi utilizado um processo de moagem para desaglomeração parcial destas partículas, tendo-se obtidos partículas com tamanhos na faixa entre 11,2 e 22,4 &#956;m. / In this work the comminution and passivation of U-4Zr-2Nb alloys by hydrading-dehydrading process was carried out and the kinetics of hydride formation was studied. The obtaining of the powdered material through the techniques of powder metallurgy is a key and necessary step in the manufacture of the pellet useful for providing the fabrication of the fuel plate. An alloy with composition U-4Zr-2Nb was chosen due to their high density and low alloying elements, in addition to its low thermal neutrons cross section. A volumetric Sievert equipment for comminuition of uranium alloys by the process of hydriding-dehydriding was designed and constructed. This equipment operates in an automatic mode through the data acquisition software also developed in this work. Along with the development of this equipment, other software was developed to calculate the kinetic of hydriding and the hydriding amount. Then, using this equipment, samples of the U-4Zr-2Nb alloy were heat treated, hydrided, passivated, milled and dehydrided. The developed comminution process was obtained in the temperature range of 108oC to 295oC and in the pressure range of 1.5 Bar to 2 Bar. All samples were completely hydrided, regardless of the hydriding temperature. The hydriding time ranged from 540 to 16176 seconds, according to the temperature used, being faster at higher temperature. Regardless of the previously heat treatments, all samples showed only the &#945; phase and, consequently, all hydridings were massive performed. It was also developed a passivation process of the obtained powder, and the powdered samples were stable, not pyrophoric and no kind of reaction was observed when exposed to air, without an excessive oxidation. In this case, it was used a gas mixture of 90% argon and 10% oxygen. After passivation, the hydride were milled and passivated again to obtain the metallic powder. The final size of the powdered metal did not depend on the heat treatment of the sample or on the hydriding temperature. The larger particles revealed to be an agglomerate of particles and therefore the milling process partially dismantle these agglomerates into primary particles. The particles size ranged from 11.2 up to 22.4 &#956;m.

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