It is important to optimize glass compositions for their specific purpose but also for the efficiency of the production process, the manufacturing of glass. This will be beneficial economically and environmentally. Today many processes and glass compositions are already optimized, but due to more strict legislation on toxic elements and substances there must be changes in many glass compositions. One of these elements is antimony; the oxide is used as fining agent to obtain a bubble free glass within a reasonable process time. One aim with this thesis is to obtain a deeper understanding of the fining mechanism in 20R2O-10MO-70SiO2 (R=Na and/or K, M = Ca and/or Ba, Mg, Sr) glasses in order to minimise the amount of Sb2O3. Another intention is to study the structure of 20R2O-10CaO-70SiO2 (R = Na, K) with Cu2+ as probe ion and thus get a deeper knowledge of the surrounding glass matrix.  The optical basicity scale is used to determine the acid/base character of the different glass compositions.   Fining efficiency results showed a remarkable increase of the number of remaining bubbles when the glass contains either approximately equal amounts of Na and K or Ca and Ba, Mg or Sr. The much higher number of bubbles in the potassium containing glasses compared to the sodium containing is explained by the increase in viscosity, the increase in optical basicity and thus lower oxygen activity. The differences in the fining efficiency when altering alkaline earth ions cannot be explained by the optical basicity values, it seems to be a more complicated situation.   This thesis also reports maximum in Vickers hardness and packing density as well as minimum in glass transition temperature for the mixed alkali glasses. The mixed alkaline earth glasses do not exhibit any clear nonlinear behaviour. Raman spectroscopy measurements showed a variation in the network connectivity which has a clear relation to the optical basicity of the different glass compositions. The combination of UV-Vis-NIR and X-ray absorption spectroscopy measurements showed that the coordination sphere for Cu(II) is a tetragonal distorted octahedron with two elongated Cu-O bonds along the z axis. There were no trends in the degree of tetragonal distortion, thus it was about the same for all the investigated glass compositions. Cu(I) is found to be coordinated by two oxygen ligands in mainly linear coordination sphere, evidenced from X-ray absorption spectroscopy.

This work has two interlocking themes. It is primarily concerned with the development of precise, broad band, Fourier transform spectrometric techniques for the determination of the optical constants of solids at millimetre and submillimetre wavelengths. One such technique cannot easily accomodate the wide range of optical constants found in solids, leading to specimens which range from the virtually transparent to the virtually opaque, and it was therefore necessary to develop transmission and reflection techniques. The intercomparison of these techniques, their particular experimental difficulties and susceptibilities to random and systematic error, was performed by using each method to determin'the optical constants of soda lime silica glass over as wide a spectral range as possible. Previous to this work there had been no systematic study of this important material at these wavelengths and,thus, this investigation gave the second theme of this work, the quantitative determination of the optical constants of soda lime silica glass at millimetre and submillimetre wavelengths. The results of this study are presented in four chapters. First, in chapter 5, power transmission Fourier transform spectrometry has been used to investigate the spectral variation of the optical constants of the glass between 3 and 50cm, using an analysis of channel spectra to give the refractive index. This chapter also contains the results of measurements made with a grating instrument between 1000 and k000cm. Secondly, in chapter 6, the results of the first direct determinations of the optical constants by dispersive transmission Fourier transform spectrometry are presented and shown to indicate the presence of a hitherto unknown loss process below 20er that is tentatively associated with a similar process previously observed in fused silica. Thirdly, in chapter 7, dispersive reflection Fourier transform spectrometry has been used to determin the optical constants up to 360em, well into the midinfrared region of opacity of this glass. The results of chapters 6 and 7 provide the first quantitative description of the optical constants of this glass betweem 3 and 360em Finally, in chapter 8, the dispersive reflection measurements are extended to simple binary and ternary silicate glasses, and these results used to identify the contributions to the mid-infrared absorption of the metal ions associated with the various metal oxide additives of the glass. From this it was possible to account for all of the absorption in soda lime silica glass as a superposition of contributions from the near-infrared bands of the SiO1 network of the glass and the four main metal ions.

Dans cette thèse, on a étudié les effets provoqués par des changements de composition et de température sur la structure et les propriétés des verres des systèmes TiO₂-SiO₂ et Na₂O-TiO₂-SiO₂. On a également examiné la réponse des verres du système Na₂O-TiO₂-SiO₂ à la déformation plastique. On a fabriqué des verres (x)TiO₂-(1-x)SiO₂ par le procédé sol-gel avec des compositions de 0 ≤ x ≤ 10 mol%, puis on les a comparés avec des verres commerciaux fabriqués par la déposition provoquée par l'hydrolyse à la flamme x = 0 ; 5,4 ; et 8,3 mol%. On a fabriqué des verres (x) Na₂O - (y) TiO₂ - (1-x-y) SiO₂ avec x = 10, 15, 20, et 25 mol% et y = 4, 7, and 10 mol% par trempage depuis l'état fondu. On a mesuré la densité des verres en utilisant le principe d'Archimède et on a mesuré l'indice de réfraction des verres par prisme coupleur. On a évalué la température de transition vitreuse des verres Na₂O-TiO₂-SiO₂ par analyse thermique différentielle. On a étudié la structure et les modules d'élasticité par spectroscopie Raman et par diffusion Brillouin, respectivement, à température ambiante et in situ jusqu'à 1 200 °C pour les verres TiO₂-SiO₂ et jusqu'à 800 °C pour les verres Na₂O-TiO₂-SiO₂. On a constaté que le module de Young des verres TiO₂-SiO₂ a diminué de 72GPa à 66 GPa avec l'addition de 8,3 mol% TiO₂, et que le module de Young des verres 10 Na₂O - (0-10) TiO₂-SiO₂ a augmenté de 65 GPa à 73 GPa avec l'addition de 10 mol% TiO₂. On a vu que l'addition de TiO₂ aux verres TiO₂-SiO₂ a décalé les sommets du spectre Raman de 460, 490, et 600 cm-1 aux fréquences plus basses, ce qui suggère un réseau structural plus ouverte et flexible ; et que l'addition de TiO₂ aux verres Na₂O-TiO₂-SiO₂ a décalé les sommets du spectre Raman 720, 800, et 840 cm-1 aux fréquences plus élevées, ce qui suggère une réduction de volume libre et un réseau structural plus rigide. L'addition de TiO₂ n'a que peu d'effet sur la réponse thermique des modules élastiques des deux systèmes, mais elle diminue l'expansion thermique et augmente les décalages de fréquences des sommets Raman de 950 and 1100 cm-1 du système TiO₂-SiO₂, alors que l'expansion thermique du système Na₂O-TiO₂-SiO₂ augmente avec les premières additions de TiO₂ et puis reste constante. Les changements de structure et de propriétés liés à la composition sont examinés, et des modèles structuraux sont proposés. La réduction d'expansion thermique et des modules d'élasticité des verres TiO₂-SiO₂ se produit par la promotion des rotations coopératives inter-tétraèdres facilitées par les liaisons Ti-O plus longues et plus faibles. L'augmentation des modules d'élasticité des verres Na₂O-TiO₂-SiO₂ est due à la formation de petits groupes avec des concentrations élevées de Na et Ti, produit par l'adoption de Ti d'une coordination quintuple d'une géométrie de pyramide à base carrée. Ces petites « globules » protègent le réseau silice des oxygènes non-pontants tout en augmentant la densité des liaisons du verre. On a étudié la réponse des verres Na₂O-TiO₂-SiO₂ au dommage mécanique et la déformation plastique par des essais d'indentation Vickers de charges de 10 mN to 49 N. La dureté de fracture a été mesurée sur éprouvette préfissurée sur une seule face (méthode SEPB). On a examiné les volumes de déformation permanente auprès des indentations Vickers par microscopie à force atomique. Les indentations Vickers ont changé d'un mélange de radial/médian et des fissures coniques à un mélange de radial/médian et des fissures latérales, suivant l'augmentation du coefficient de Poisson. Avec la croissance du coefficient de Poisson, la dureté de verre diminue de 5,5 GPa à 4,5 GPa ; la longueur moyenne de fissure radial/médian double, à peu près ; et la dureté de fracture reste constante. Le volume de verre déformé par l'écoulement de cisaillement augmente petit à petit avec l'augmentation du coefficient de Poisson et devient plus grand que le volume densifié à ν =0,237. / The responses of structure and properties to composition and temperature have been investigated for glasses in TiO₂-SiO₂ and Na₂O-TiO₂-SiO₂ systems. Additionally, the response of Na₂O-TiO₂-SiO₂ glasses to plastic deformation has been studied. (x)TiO₂-(1-x)SiO₂ glasses were prepared through the sol-gel process with compositions 0 ≤ x ≤ 10 mol% and compared to commercial glasses prepared through flame hydrolysis deposition with x = 0, 5.4, and 8.3 mol%. (x) Na₂O - (y) TiO₂ - (1-x-y) SiO₂ glasses were prepared with x = 10, 15, 20, and 25 mol% and y = 4, 7, and 10 mol% through a melt-quench process. Density and index of refraction of glasses was measured through the Archimedes's method and using a prism coupler, respectively. The glass transition temperature of Na₂O-TiO₂-SiO₂ glasses was measured through differential thermal analysis. The structure and elastic moduli have been studied through Raman spectroscopy and Brillouin light scattering, respectively, at room temperature and in-situ up to 1200 °C for TiO₂-SiO₂ glasses and up to 800 °C for Na₂O-TiO₂-SiO₂ glasses. Young's modulus was observed to decrease from 72 GPa to 66 GPa with the addition of 8.3 mol% TiO₂ in TiO₂-SiO₂ glasses and to increase from 65 GPa to 73 GPa with the addition of 10 mol% TiO₂ in 10 Na₂O - (0-10) TiO₂-SiO₂ glasses. The addition of TiO₂ was observed to shift the 460, 490, and 600 cm-1 Raman peaks to lower frequencies in TiO₂-SiO₂ glasses, suggesting a more open and flexible network, and the 720, 800, and 840 cm-1 Raman peaks to higher frequencies in Na₂O-TiO₂-SiO₂ glasses, suggesting a lower free volume and stiffer network. The addition of TiO₂ has little effect on the temperature response of the elastic moduli in either system, but decreases the thermal expansion and increases the frequency shifts in the 950 and 1100 cm-1 Raman peaks in the TiO₂-SiO₂ system while the thermal expansion increases with initial additions of TiO₂ and then remains constant in the Na₂O-TiO₂-SiO₂ system. Changes in structure and property with composition have been discussed, and structural models were proposed. The reduction of thermal expansion and elastic moduli in TiO₂-SiO₂ glasses occurs through the promotion of cooperative, inter-tetrahedral rotations facilitated by the longer and weaker Ti-O bonds. The increase in elastic moduli in the Na₂O-TiO₂-SiO₂ glasses occurs through the formation of small clusters with local, relatively high Ti and Na concentrations, promoted by Ti adopting a five-fold coordination in a square-pyramidal geometry. These clusters work to shield the silica network from non-bridging oxygens from the presence of Na while simultaneously increasing the volume bond density of the glass. For Na₂O-TiO₂-SiO₂ glasses, the response to mechanical damage and plastic deformation has been examined through Vickers indentation experiments at loads from 10 mN to 49 N. Fracture toughness was measured through the single-edge precracked beam method. The permanent deformation volumes around Vickers indents were investigated through atomic force microscopy. Critical loads for crack initiation and cracking patterns were systematically investigated and correlated with the elastic properties of glass. Vickers indents were observed to change from a mixture of radial/median and cone cracks to radial/median and lateral cracks as Poisson's ratio increases. As Poisson's ratio increases hardness decreases from 5.5 GPa to 4.5 GPa, the average radial/median crack length roughly doubles, and fracture toughness remains constant. A minimum in the critical crack initiation load was observed at ν = 0.21-0.22. The volume of glass deformed through shear flow increases gradually with increasing Poisson's ratio, becomes larger than the densified volume at ν =0.237.

Made available in DSpace on 2014-06-11T19:25:31Z (GMT). No. of bitstreams: 0 Previous issue date: 2011-02-17Bitstream added on 2014-06-13T19:12:21Z : No. of bitstreams: 1 escanhoelajunior_ca_me_rcla.pdf: 2205069 bytes, checksum: 07cd01b4a104f262986c24bd2a7f874b (MD5) / Fundação de Amparo à Pesquisa do Estado de São Paulo (FAPESP) / Neste trabalho realizamos a polarização térmica em vidros silicatos com composição (%mol) 22Na2O.8CaO.65SiO2 .5MO2 (M = Si, Ti, Ge, Zr, Sn e Ce). A polarização térmica consiste em aplicar um campo elétrico DC de elevada intensidade (~1 MV/m) em amostras a altas temperaturas. Durante a polarização térmica é gerado um campo elétrico permanente no interior da amostra, na região do anodo, que é responsável por propriedades ópticas nãolineares. Submetemos à polarização térmica amostras dos vidros, com ~1,5 mm de espessura e área de 20 x 20 mm2. Utilizamos eletrodos de Au, com diâmetro de 1 cm. As amostras foram aquecidas no interior de um forno até ~145 oC e aplicamos um campo elétrico de 1 MV/m durante 60 min. Durante a aplicação do campo elétrico, medimos simultaneamente a corrente através do circuito e as temperaturas no forno e na amostra. A corrente elétrica medida no circuito está relacionada com a migração de íons Na+ no interior das amostras do anodo para o catodo. A diminuição da corrente após um determinado tempo de polarização é devido à formação de uma camada com ausência de íons Na+ (camada de depleção) junto ao anodo. Os diferentes cátions tetravalentes, M4+, inseridos no vidro têm funções particulares na estrutura deste e afetam de formas distintas a corrente elétrica. A energia de ativação para a condutividade elétrica em vidros soda-cal-sílica está associada à energia necessária para o íon Na+ transpor a barreira de potencial entre os interstícios adjacentes na rede vítrea. Para determinar a energia de ativação da condutividade elétrica DC, Eσ, destes vidros, submetemos amostras de cada composição a um campo elétrico de 1 MV/m, durante 2 segundos para diferentes temperaturas entre 100 e 220 ºC. Esta energia está relacionada com... / In this work we performed thermal poling in glasses with composition (%mol) 22Na2O.8CaO.65SiO2 .5MO2 (M = Si, Ti, Ge, Zr, Sn and Ce). The thermal poling consist in apply a high intensity DC electric field (~1 MV/m) on samples at high temperatures. During the thermal poling process a permanent electric field is generated in the anode region of the sample, and this field is responsible for nonlinear optical properties of various glasses. We submit to thermal poling samples with ~1.5 mm in thickness and area of 20x20 mm2. We used gold electrodes with a diameter of 1 cm. The samples were heated inside a furnace to ~ 145 oC and an electric field of 1 MV/m was applied for 60 min. During the poling process, we measure simultaneously the current through the circuit and the temperatures in the furnace and of the sample. The electric current of the circuit is related to the migration of sodium ions in the bulk samples from the anode to the cathode. The current decrease with the poling time is due to the formation of a Na+ absent layer (depletion layer) near the anode surface. The different tetravalent cations, M4+, in the glass have different functions in their structures and affect the electrical current in particular manners. The activation energy for electrical conductivity in soda-lime-silica glasses is associated with energy for the Na+ ions to cross the potential barrier, which is submitted to the interstices of the glassy network, and jump into the nearest interstice. The activation energy of DC electrical conductivity, Eσ, of our samples of was determined by applying an electric field of 1 MV/m for 2 seconds, at different temperatures between 100 and 220 ºC. This energy is related to the current, I, through the equation ... The energy calculated is ~0.8 eV. To evaluate the structural and compositional changes of the samples surfaces that were in contact with the ...

Orientador: Ervino Carlos Ziemath / Banca: Dante Luis Chinaglia / Banca: Victor Ciro Solano Reynoso / Resumo: Neste trabalho realizamos a polarização térmica em vidros silicatos com composição (%mol) 22Na2O.8CaO.65SiO2 .5MO2 (M = Si, Ti, Ge, Zr, Sn e Ce). A polarização térmica consiste em aplicar um campo elétrico DC de elevada intensidade (~1 MV/m) em amostras a altas temperaturas. Durante a polarização térmica é gerado um campo elétrico permanente no interior da amostra, na região do anodo, que é responsável por propriedades ópticas nãolineares. Submetemos à polarização térmica amostras dos vidros, com ~1,5 mm de espessura e área de 20 x 20 mm2. Utilizamos eletrodos de Au, com diâmetro de 1 cm. As amostras foram aquecidas no interior de um forno até ~145 oC e aplicamos um campo elétrico de 1 MV/m durante 60 min. Durante a aplicação do campo elétrico, medimos simultaneamente a corrente através do circuito e as temperaturas no forno e na amostra. A corrente elétrica medida no circuito está relacionada com a migração de íons Na+ no interior das amostras do anodo para o catodo. A diminuição da corrente após um determinado tempo de polarização é devido à formação de uma camada com ausência de íons Na+ (camada de depleção) junto ao anodo. Os diferentes cátions tetravalentes, M4+, inseridos no vidro têm funções particulares na estrutura deste e afetam de formas distintas a corrente elétrica. A energia de ativação para a condutividade elétrica em vidros soda-cal-sílica está associada à energia necessária para o íon Na+ transpor a barreira de potencial entre os interstícios adjacentes na rede vítrea. Para determinar a energia de ativação da condutividade elétrica DC, Eσ, destes vidros, submetemos amostras de cada composição a um campo elétrico de 1 MV/m, durante 2 segundos para diferentes temperaturas entre 100 e 220 ºC. Esta energia está relacionada com... (Resumo completo, clicar acesso eletrônico abaixo) / Abstract: In this work we performed thermal poling in glasses with composition (%mol) 22Na2O.8CaO.65SiO2 .5MO2 (M = Si, Ti, Ge, Zr, Sn and Ce). The thermal poling consist in apply a high intensity DC electric field (~1 MV/m) on samples at high temperatures. During the thermal poling process a permanent electric field is generated in the anode region of the sample, and this field is responsible for nonlinear optical properties of various glasses. We submit to thermal poling samples with ~1.5 mm in thickness and area of 20x20 mm2. We used gold electrodes with a diameter of 1 cm. The samples were heated inside a furnace to ~ 145 oC and an electric field of 1 MV/m was applied for 60 min. During the poling process, we measure simultaneously the current through the circuit and the temperatures in the furnace and of the sample. The electric current of the circuit is related to the migration of sodium ions in the bulk samples from the anode to the cathode. The current decrease with the poling time is due to the formation of a Na+ absent layer (depletion layer) near the anode surface. The different tetravalent cations, M4+, in the glass have different functions in their structures and affect the electrical current in particular manners. The activation energy for electrical conductivity in soda-lime-silica glasses is associated with energy for the Na+ ions to cross the potential barrier, which is submitted to the interstices of the glassy network, and jump into the nearest interstice. The activation energy of DC electrical conductivity, Eσ, of our samples of was determined by applying an electric field of 1 MV/m for 2 seconds, at different temperatures between 100 and 220 ºC. This energy is related to the current, I, through the equation ... The energy calculated is ~0.8 eV. To evaluate the structural and compositional changes of the samples surfaces that were in contact with the ... / Mestre

O vidro com composição 2Na2O1CaO3SiO2, sofre nucleação cristalina homogênea em temperaturas entre 450 e 560oC. Os núcleos, essencialmente esféricos, supostamente tem a mesma composição da matriz vítrea. Em amostras amorfas, parcialmente cristalizadas e policristalinas foram feitas medidas de densidade, difratometria de raios-X, analise térmica por calorimetria exploratória de varredura (DSC), medidas ultrasônicas pelo método do pulso-eco, espectroscopias de absorção ótica, infravermelha e Raman. A densidade do vidro é de 2,66 g/cm3 e para amostra policristalina a densidade aumenta para 2,76 g/cm3. O aumento da densidade com o grau de cristalinidade é a causa do aumento das velocidades de propagação de ondas elásticas longitudinal e transversal, e do aumento do numero e da intensidade dos picos nos difratogramas de raios-X. Das medidas de DSC determinamos que a temperatura de transição vítrea ocorre em torno de 40 °C, e calculamos uma entalpia de ativação para a transição vítrea de 78 kcal/mol. Espectros de absorção ótica de amostras com Cr3+ apresentaram o efeito de anti-ressonância Fano, e pequeno deslocamento da banda 4T2 , para energias maiores com o aumento do grau de cristalinidade e em temperaturas baixas (~ 20 K). A partir dos níveis isoenergéticos 2E e 2T1 calculamos o parâmetro de Racah B = 690 cm-1 e a intensidade do campo ligante ? = 10 Dq = 14 840 cm-1. Junto com Cr3+ ocorre o Cr6+ na forma do íon cromato, CrO42-, cujas bandas de absorção estão próximas do ultravioleta, e é responsável pelo efeito Raman pré-ressonante observado. O espectro Raman do vidro é constituído de bandas assimétricas acima de 550 cm-1, e foram decompostas em seis bandas gaussianas. As bandas de maior freqüência foram tentativamente atribuídas à vibrações de tetraedros de sílica com 1 a 4 oxigênios não-ponteantes. Dos espectros Raman reduzidos concluímos que o pico de boson é devido à vibrações dos fônons térmicos o a freqüência da radiação espalhada. Algumas características dos espectros de absorção de amostras com Cr3+ e dos resultados de medidas ultrasônicas foram atribuídas à possível ocorrência de microtensão ou microfissuras na região da interface núcleo-vidro. / Glass with composition 2Na2O1CaO3SiO2, undergoes homogeneous crystal nucleation between 450 and 56OoC. The nuclei are essentially spherical and presumable have the same composition as the glass matrix. Measuriments of density, X-ray diffraction, thermal analysis by differential scanning calorimetry (DSC), ultrasonics by pulse-echo method, optical absorption, infrared and Raman spectroscopy were performed in amorphous, partially crystallized and polycrystalline samples. The density of the glass is 2,66 g/cm3 and 2,76 g/cm3 that of the polycrystalline sample. The increase in density with the degree of crystallinity is the cause of the increasing propagation velocities of longitudinal and transversal elastic waves, and of the increasing peak number and intensities in the X-ray diffractograms. From DSC measurements we determine that the glass transition temperature is about 470o C, and the activation enthalpy for the glass transition was calculated to be 78 kcal/mol. Absorption spectra of Cr3+ containing samples shows the anti-resonance Fano effect, and small displacement of the 4T2 band to higher energies with increasing degree of crystallinity and at lower temperatures (~20 K). From the isoenergetic levels 2E and 2T1 we calculate the Racah parameter B = 690 cm-1 and the ligand field intensity ? = 10 Dq = 14 840 cm-1. Together with Cr3+ occurs Cr6+ as cromate ion, CrO4-2 with absorption bands are near the ultraviolet, and is responsible for the observed pre-resonant Raman effect. The Raman spectrum of the glass is composed of asimetric bands in frequencies above 550 cm-1, which we decompose in six Gaussian shaped bands. The four bands of higher frequencies were tentativily assigned to stretching vibration bond Si-O of silica tetraedra with 1 to 4 non-bridging oxigens. From reduced Raman spectra we concluded that the boson peak is due to thermal phonon vibrations and to the scattered radiation frequency. Some features of absorption spectra of Cr3+ containing glasses and of ultrasonic measurements were assigned to the possible occurence of microtensions or microcracks in the nucleous-glass interf ace region.

O vidro com composição 2Na2O1CaO3SiO2, sofre nucleação cristalina homogênea em temperaturas entre 450 e 560oC. Os núcleos, essencialmente esféricos, supostamente tem a mesma composição da matriz vítrea. Em amostras amorfas, parcialmente cristalizadas e policristalinas foram feitas medidas de densidade, difratometria de raios-X, analise térmica por calorimetria exploratória de varredura (DSC), medidas ultrasônicas pelo método do pulso-eco, espectroscopias de absorção ótica, infravermelha e Raman. A densidade do vidro é de 2,66 g/cm3 e para amostra policristalina a densidade aumenta para 2,76 g/cm3. O aumento da densidade com o grau de cristalinidade é a causa do aumento das velocidades de propagação de ondas elásticas longitudinal e transversal, e do aumento do numero e da intensidade dos picos nos difratogramas de raios-X. Das medidas de DSC determinamos que a temperatura de transição vítrea ocorre em torno de 40 °C, e calculamos uma entalpia de ativação para a transição vítrea de 78 kcal/mol. Espectros de absorção ótica de amostras com Cr3+ apresentaram o efeito de anti-ressonância Fano, e pequeno deslocamento da banda 4T2 , para energias maiores com o aumento do grau de cristalinidade e em temperaturas baixas (~ 20 K). A partir dos níveis isoenergéticos 2E e 2T1 calculamos o parâmetro de Racah B = 690 cm-1 e a intensidade do campo ligante ? = 10 Dq = 14 840 cm-1. Junto com Cr3+ ocorre o Cr6+ na forma do íon cromato, CrO42-, cujas bandas de absorção estão próximas do ultravioleta, e é responsável pelo efeito Raman pré-ressonante observado. O espectro Raman do vidro é constituído de bandas assimétricas acima de 550 cm-1, e foram decompostas em seis bandas gaussianas. As bandas de maior freqüência foram tentativamente atribuídas à vibrações de tetraedros de sílica com 1 a 4 oxigênios não-ponteantes. Dos espectros Raman reduzidos concluímos que o pico de boson é devido à vibrações dos fônons térmicos o a freqüência da radiação espalhada. Algumas características dos espectros de absorção de amostras com Cr3+ e dos resultados de medidas ultrasônicas foram atribuídas à possível ocorrência de microtensão ou microfissuras na região da interface núcleo-vidro. / Glass with composition 2Na2O1CaO3SiO2, undergoes homogeneous crystal nucleation between 450 and 56OoC. The nuclei are essentially spherical and presumable have the same composition as the glass matrix. Measuriments of density, X-ray diffraction, thermal analysis by differential scanning calorimetry (DSC), ultrasonics by pulse-echo method, optical absorption, infrared and Raman spectroscopy were performed in amorphous, partially crystallized and polycrystalline samples. The density of the glass is 2,66 g/cm3 and 2,76 g/cm3 that of the polycrystalline sample. The increase in density with the degree of crystallinity is the cause of the increasing propagation velocities of longitudinal and transversal elastic waves, and of the increasing peak number and intensities in the X-ray diffractograms. From DSC measurements we determine that the glass transition temperature is about 470o C, and the activation enthalpy for the glass transition was calculated to be 78 kcal/mol. Absorption spectra of Cr3+ containing samples shows the anti-resonance Fano effect, and small displacement of the 4T2 band to higher energies with increasing degree of crystallinity and at lower temperatures (~20 K). From the isoenergetic levels 2E and 2T1 we calculate the Racah parameter B = 690 cm-1 and the ligand field intensity ? = 10 Dq = 14 840 cm-1. Together with Cr3+ occurs Cr6+ as cromate ion, CrO4-2 with absorption bands are near the ultraviolet, and is responsible for the observed pre-resonant Raman effect. The Raman spectrum of the glass is composed of asimetric bands in frequencies above 550 cm-1, which we decompose in six Gaussian shaped bands. The four bands of higher frequencies were tentativily assigned to stretching vibration bond Si-O of silica tetraedra with 1 to 4 non-bridging oxigens. From reduced Raman spectra we concluded that the boson peak is due to thermal phonon vibrations and to the scattered radiation frequency. Some features of absorption spectra of Cr3+ containing glasses and of ultrasonic measurements were assigned to the possible occurence of microtensions or microcracks in the nucleous-glass interf ace region.

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Le magnésium est l'un des quatre éléments majeurs sur Terre. Il est présent dans différentes proportions dans les verres industriels et naturels (jusqu'à 30 poids% dans les komatiites, verres ultramafiques d'âge archéen). Sa présence semble influencer les propriétés physico-chimiques des verres et tout spécialement leur durabilité. Malgré ce comportement, le magnésium a été relativement peu étudié dans les verres et les études précédentes ont conduit à des contradictions sur son environnement (coordinence 4 et 6 par RMN et en coordinence 5 par diffraction des neutrons). Dans le but de lever ces contradictions, l'étude de la structure des verres magnésio-silicatés et de l'environnement du magnésium a été réalisée en utilisant deux méthodes complémentaires : la spectrométrie Raman et la spectroscopie d'absorption des rayons X. La spectroscopie Raman permet d'obtenir des informations sur la structure des verres telle que la connectivité du réseau silicaté, la variation des angles Si-O-Si ou la modification de la taille des anneaux de silicium. Plus précisément, les variations de la région des spectres Raman comprise entre 800 et 1400 cm-1 illustrent l'évolution du degré de polymérisation des verres en fonction du taux de magnésium, du taux de silicium et de la nature de l'alcalin modificateur de réseau. La spectroscopie d'absorption des rayons X au seuil K du magnésium nous a permis d'accéder à l'environnement spécifique autour de cet ion. Les spectres XANES des verres ont été comparés à ceux de références cristallines contenant du magnésium dans différents environnements (coordinence et nature des voisins notamment). Pour aller au-delà de la méthode dite « d'empreinte digitale », et extraire des informations structurales pertinentes, les spectres XANES des cristaux et des verres ont été calculés. Les calculs ont été réalisés avec un code basé sur une méthode en ondes planes, dans l'espace réciproque avec l'utilisation de potentiel non muffin-tin. L'utilisation des calculs a permis de mettre en évidence des paramètres structuraux pertinents pour expliquer la position des structures XANES. Pour les verres, les structures initiales utilisées pour les calculs ont été obtenus par dynamique moléculaire classique puis relaxée de façon ab initio. L'environnement du magnésium (coordinence/distorsion) peut varier en fonction de la composition du verre. De ce fait, les interprétations classiquement réalisées des spectres Raman des verres doivent être considérées avec précaution / The structure of magnesio-silicate glasses have been studied by using two complementray spectroscopic methods : (i) The Raman spectroscopy allows to obtain information on the silicate network and on the network connectivity. The variations of the region between 800 and 1400 cm?¹ show the evolution of the polymerization degree as a function of various compositions. (ii) The local environment of the magnesium has been investigated by X-ray absorption spectroscopy at the Mg K-edge. The XANES spectra have been compared with the spectra of model compounds containing magnesium in different environments. As it is not straightforward to extract relevant structural information of crystalline model compound spectra by the "fingerprint" method, we have used ab initio calculations based on the planewave method. The results obtained by calculations have allowed us to connect relevant structural characteristics with the positions of the XANES features