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Estudos experimentais recentes revelaram que os compostos Mn[As(1-x) Sb(x)] e La[Fe(x) Si(1-x)]13 apresentam grandes valores para a variação isométrica da entropia e para a variação adiabática da temperatura. Estudos experimetais também mostram que o efeito magnetocalórico nestes compostos pode ser facilmente controlado através da dopagem e da pressão externa. Logo, tais dados experimentais, que necessitam de uma descrição teórica, indicam que estes compostos são bons candidatos para se estudar também o efeito barocalórico. Nesta tese, estudamos do ponto de vista teórico o efeito magnetocalórico nos compostos La[Fe(x)Si(1-x)]13 e Mn[As(1-x) Sb(x)], a pressão ambiente e a pressões externas. Estudamos também o efeito barocalórico, para alguns valores fixos do campo magnético. Este estudo teórico foi feito utilizando três modelos, a saber: (1) um modelo itinerante, de uma única rede.(2) um modelo itinerante mais elaborado com duas subredes incluindo a desordem química em uma das subredes. (3) um modelo de monentos localizados. Nossos resultados mostram que os dados experimentais dos potenciais magnetocalóricos são bem explicados pelos três modelos. Entretanto, o modelo com duas subredes é o que melhor descreve os mecanismos físicos envolvidos no efeito magnetocalórico dos compostos estudados. O modelo de monentos magnéticos localizados falha na explicação da entropia magnética a altas temperaturas e na magnetização de saturação a T= 0 K. O modelo itinerante, com uma única rede, não descreve corretamente a transferência eletrônica entre as subredes. / Recent experimental data revealed that the compounds La[Fe(x)Si(1-x)]13 and Mn[As(1-x)Sb(x)], present great values for the isothermal entropy change and the adiabatic temperature change. They also showed that the magnetocaloric effect in these compounds can be easily tuned through doping and external pressure. Therefore, such experimental data, which need a theoretical description indicate that these compounds are also good candidates to study the barocaloric effect. In this PhD thesis, we studied from the theoretical point of view the magnetocaloric effect in the compounds La[Fe(x)Si(1-x)]13 and Mn[As(1-x)Sb(x)], at ambient pressure and upon external pressures. We also studied the barocaloric effect,for some fixed values of the model, of only one lattice.(2)a more elaborated itinerant model with two sublattices including the chemical disorder in one sulattice. (3) model of localized magnetic moments. Our results show that the available experimental data of the magnetocaloric potentials are well explained by the three models. However, only the two sublattice itinerant model properly describes the physical mechanisms involved in the magnetocaloric effect of the studied compounds.The localized magnetic moment model fails in explaining the magnetic entropy at high temperatures and the saturation magnetization at T = 0 K. The effective one lattice itinerant model does not properly describe the eletronic transfer between the sublattices.

Les revêtements galvanisés alliés sont produits par immersion à chaud d’une bande d'acier dans un bain de zinc fondu à environ 460 °C, saturé en fer et contenant de faibles quantités d'aluminium (de 0,1 à 0,135% poids), suivie d’un traitement thermique (jusqu'à des températures voisines de 500-530 °C pendant environ 10 s) afin de déclencher les réactions d'alliation entre le fer et le zinc. La microstructure finale de ce type de revêtement est composée d'une succession de couches stratifiées de phases Fe-Zn et ses propriétés d'usage sont directement liées à la distribution de ces phases dans le revêtement. Les paramètres process à appliquer sur ligne industrielle doivent donc être optimisés pour obtenir la microstructure de revêtement souhaitée avec des coûts minimaux. Le développement d'un tel revêtement passe par différentes réactions complexes : la formation de la couche d'inhibition, la rupture de cette couche, la consommation du zinc liquide et l'enrichissement en fer du revêtement solide. Les cinétiques de ces réactions doivent être étudiées et modélisées séparément afin de contrôler avec précision l'évolution du revêtement au cours du cycle thermique. Dans ce travail, les deux premières réactions ont été étudiées dans le cas des aciers IF Ti. La cinétique de formation de la couche d'inhibition est extrêmement rapide et n’a par conséquent pas été étudiée. L'attention a été portée sur la nature de cette couche et sur les mécanismes responsables de sa formation. Il a été démontré que la couche d'inhibition formée dans des bains classiques pour la production de ces revêtements est composée d'une première couche très mince de Fe2Al5Znx (20-30 nm) sur la surface de l’acier et d’une seconde couche plus épaisse de δ (FeZn7) (environ 200 nm) au-dessus. Lorsque l'acier est immergé dans le bain de zinc, la dissolution du premier dans le second conduit à une sursaturation en fer à l'interface solide / liquide. Une très fine couche de Fe2Al5Znx métastable germe alors sur la surface de l'acier favorisée par des relations préférentielles d’épitaxie avec la ferrite. Par la suite, une couche de δ germe sur la couche de Fe2Al5Znx ce qui permet à la microstructure finale de devenir thermodynamiquement stable. L'effet de la teneur en aluminium du bain sur la nature de la couche d'inhibition a également été étudié. Quand la teneur en aluminium du bain diminue, la couche de Fe2Al5Znx devient discontinue car cette phase devient plus métastable et sa germination sur la surface de l'acier moins probable. Cette étape d’inhibition n'est que transitoire et un traitement thermique prolongé conduira à la rupture de la couche d'inhibition et au développement des réactions Fe-Zn. Le mécanisme de rupture, contrôlé par la diffusion du zinc dans les joints de grains de l'acier, peut être expliqué à l'aide du diagramme de phase ternaire Al-Fe-Zn et résumé en deux étapes : la disparition de la couche de Fe2Al5Znx à l'interface couche d’inhibition / acier résultant de l’enrichissement de cette interface en zinc, et la germination de la phase Г (Fe3Zn10) aux joints de grains de l'acier lorsque la concentration en zinc y devient suffisante. C’est cette germination qui va provoquer localement la rupture de la couche d’inhibition. La cinétique de cette réaction dépend fortement de la composition chimique de l'acier IF Ti et de la teneur en aluminium du bain. D'une part, il apparaît que l'effet de la composition chimique de l'acier sur la cinétique de rupture d'inhibition est contrôlé par la compétition entre deux phénomènes opposés : la vitesse de diffusion du zinc dans les joints de grains de l'acier et la capacité de l'acier à y accumuler les atomes de zinc. D'autre part, la diminution de la teneur en aluminium du bain favorise la discontinuité de la couche de Fe2Al5Znx, ce qui accélère la rupture de la couche d'inhibition car le zinc est supposé diffuser plus rapidement dans δ que dans Fe2Al5Znx. / Hot-Dip GalvAnnealed (HDGA) coatings are produced by the immersion of the steel strip into an iron-saturated liquid zinc bath at around 460 °C containing small amounts of aluminium (from 0.1 to 0.135 wt.%, normally) and its subsequent heating (up to temperatures around 500-530 °C for about 10 s, typically) in order to trigger the alloying reactions between iron and zinc. The final microstructure of this kind of coatings is composed of a sequence of stratified Fe-Zn phase layers and its in-use properties are directly related to the phase distribution within the coating. The process parameters to be performed in industrial lines must therefore be optimized in order to obtain a successful coating microstructure with the minimum costs. The development of such a coating passes through different and complex reactions: the inhibition layer formation, the inhibition layer breakdown, the liquid zinc consumption and the iron enrichment of the solid coating. The kinetics accounting for these reactions must be studied and modelled separately in order to accurately control the evolution of the coating along the heat treatment performed in the industrial line. In the present work, the two first reactions were investigated in the case of Ti IF steel grades. The kinetics of the inhibition layer formation is extremely fast and has therefore not been investigated in detail. Concerning this reaction, the focus was given to the nature of this inhibition layer and to the mechanisms accounting for its formation. It has been found that the inhibition layer formed in typical baths for galvannealed coatings production is composed of a very thin layer of the Fe2Al5Znx phase (20-30 nm) on the steel surface and a thicker layer of the δ (FeZn7) phase (around 200 nm) on its top. As the steel strip enters the zinc bath, iron dissolution from the former into the latter leads to an iron supersaturation at the solid / liquid interface. As a result, a very thin layer of metastable Fe2Al5Znx nucleates on the steel surface favoured by preferential epitaxial relationships with ferrite. Subsequently, δ nucleates on the Fe2Al5Znx layer allowing the final microstructure of the inhibition layer to become thermodynamically stable. The effect of the bath aluminium content on the nature of this inhibiting structure has also been studied. As the bath aluminium content is lowered, the Fe2Al5Znx layer becomes discontinuous: the lower the bath aluminium content is, the higher the metastability of Fe2Al5Znx is and the less probable its nucleation on the steel surface is. The inhibition state is only transient and continued heat treatment will lead to the inhibition layer breakdown and the development of the further Fe-Zn alloying reactions. The breakdown mechanism, controlled by the diffusion of zinc towards the steel grain boundaries, can be explained using the Al-Fe-Zn ternary phase diagram and summarized in two steps: the disappearance of the Fe2Al5Znx layer at the inhibition layer / steel interface as a result of the enrichment of this interface in zinc, and the local nucleation of the Г (Fe3Zn10) phase at the steel grain boundaries, breaking the inhibition layer off, when the zinc concentration at these locations becomes high enough. The kinetics accounting for this reaction strongly depends on the Ti IF steel chemical composition and the bath aluminium content. On the one hand, it has been found that the effect of the steel chemical composition on the inhibition layer breakdown kinetics would be ruled by the competition between two opposite phenomena: the rate of zinc diffusion at the steel grain boundaries and the ability of the steel to accumulate the zinc atoms at these locations On the other hand, decreasing the bath aluminium content favours the discontinuity of Fe2Al5Znx, which accelerates the inhibition layer breakdown as zinc is expected to diffuse faster through δ than through Fe2Al5Znx.

Orientador: Carlos Manuel Giles Antunez de Mayolo / Dissertação (mestrado) - Universidade Estadual de Campinas, Instituto de Fisica Gleb Wataghin / Made available in DSpace on 2018-08-18T09:44:07Z (GMT). No. of bitstreams: 1 Veiga_LarissaSayuriIshibe_M.pdf: 17048771 bytes, checksum: 679326ce3ab87d18e691e2a4c2789f17 (MD5) Previous issue date: 2011 / Resumo: Neste trabalho estudamos o comportamento magnético do composto Eu8Ga16Ge30, o único clatrato conhecido atualmente cujas posições hóspedes são completamente preenchidas por um elemento terra-rara. Este composto cristaliza-se em uma estrutura cúbica (grupo espacial Pm_3n), apresentando duas diferentes gaiolas formadas pelos átomos Ga-Ge (uma gaiola menor formada por 20 átomos e uma gaiola maior, formada por 24 átomos) que englobam em seu interior íons divalentes Eu+2. Os momentos magnéticos desses íons ordenam-se ferromagneticamente abaixo de TC = 36 K através da interação RKKY. O objetivo deste trabalho foi investigar o comportamento magnético local dos sítios cristalográficos ocupados pelos íons de Eu, que no interior das gaiolas maiores, situam-se em posições fora do centro destas, contidas em planos perpendiculares às faces da célula unitária cúbica. Nesta dissertação descrevemos a síntese do composto Eu8Ga16Ge30 pelo método do fluxo metálico, a caracterização da amostra através da difração de raios X de alta resolução (verificação da qualidade cristalina) e da difração de pó de raios X (determinação do parâmetro de rede). Medidas de resistividade elétrica em função da temperatura mostraram a existência de saltos relacionados ao aumento da resistividade, na temperatura de transição magnética (TC) e em T* = 24 K. O mesmo comportamento foi verificado na literatura que indica que a anomalia encontrada em T* possui origem magnética. As propriedades magnéticas foram estudadas através de medidas de grandezas macroscópicas, como susceptibilidade magnética e magnetização em função do campo magnético aplicado. O comportamento magnético local do composto foi estudado através da técnica de difração magnética ressonante com seletividade aos sítios cristalográficos ocupados pelos átomos de Eu. Esta última técnica foi capaz de fornecer informações locais sobre o magnetismo dos átomos de Eu localizados nos sítios 2a e 24k através do estudo das histereses magnéticas obtidas na condição de difração em diferentes temperaturas. Foi observado que o comportamento magnético dos sítios cristalográficos 2a e 24k são diferentes para a temperatura de 8 K, no entanto, nenhuma diferença significativa foi encontrada para as histereses dos dois sítos em T = 30 K. Verificamos que a histerese magnética do sítio 24k em 8 K é formada por várias contribuições indicando a existência de uma estrutura magnética em que os momentos magnéticos situados neste sítio encontram-se dispostos ao longo de três direções perpendiculares entre sí. Verificamos também histereses magnéticas menos estruturadas em T = 30 K que podem estar relacionadas à presença de uma estrutura magnética na qual todos os momentos magnéticos estão orientados ao longo de uma única direção (eixo de fácil magnetização, na direção [001]). No entanto, o mecanismo que descreve o comportamento magnético deste composto (reorientação de spins ou duas temperaturas de ordenamento magnético) ainda não foi totalmente elucidado / Abstract: In this work we studied the magnetic behavior of Eu8Ga16Ge30 clathrate compound, the only clathrate known so far where the guest positions are fully occupied by a rare-earth element. This compound crystallizes in a cubic unit cell (space group Pm_3n) and presents two types of cages formed by Ga-Ge atoms (a smaller cage formed by 20 atoms and a larger cage, formed by 24 atoms) inside which Eu+2 guest ions reside. The magnetic moments of these ions order ferromagnetically below TC _ 36 K through RKKY interaction. The aim of this thesis was the investigation of the local magnetic properties of the crystallographic sites occupied by Eu ions, which inside of the larger cages, are located in four off-center positions contained in planes perpendicular to the faces of the cubic unit cell. In this work we describe the synthesis process of Eu8Ga16Ge30 compound. Eu8Ga16Ge30 single crystal was grown from metallic flux method with excess of Ga. We also describe the structural characterization of the samples by high resolution x-ray diffraction and x-ray powder diffraction. Electrical resistivity measurements were performed and showed anomalies not only at TC but also at T* _ 24 K. The same behavior was observed in the literature which indicates that the anomaly found in T* has a magnetic nature. The magnetic properties were studied by macroscopic measurements such as magnetic susceptibility and magnetization versus applied magnetic field. The local magnetic behavior of the compound was probed by dichroic resonant diffraction of circularly polarized x rays. This technique was used to measure site-specific magnetism of the Eu8Ga16Ge30 compound. It was able to provide information about the magnetism of the crystallographic sites 2a and 24k occupied by Eu ions through the study of magnetic hysteresis obtained in the diffraction condition at different temperatures. It was observed that the magnetic behavior of the 2a and 24k crystallographic sites are different for the temperature of 8 K. However, no difference was found for the hysteresis of the two sites on T = 30 K. The results suggest that the magnetic hysteresis of the 24k site at 8 K is formed by several contributions indicating the existence of a magnetic structure where the magnetic moments located on this site are arranged along three mutually perpendicular directions. We also found less structured magnetic hysteresis at T = 30 K which may be related to the presence of a magnetic structure in which all magnetic moments are oriented along a single direction (easy axis of magnetization along [001]). However, the mechanism that describes the magnetic behavior of this compound (spin reorientation or two temperatures of magnetic ordering) has not been fully elucidated / Mestrado / Física Atômica e Molecular / Mestra em Física

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