Made available in DSpace on 2014-06-11T19:34:59Z (GMT). No. of bitstreams: 0 Previous issue date: 2002-10Bitstream added on 2014-06-13T18:45:52Z : No. of bitstreams: 1 graca_mla_dr_guara.pdf: 5050152 bytes, checksum: dce8c01ce72d2ebc0e9caea4d6df5d6b (MD5) / Neste trabalho foi feita uma análise detalhada dos micromecanismos de iniciação da fratura em amostras entalhadas para cinco aços e duas ligas de alumínio. Com esse objetivo foram obtidas curvas de transição frágil-dúctil e de tenacidade à fratura em função do raio da raiz do entalhe, e realizados ensaios interrompidos antes da fratura da amostra. Análises fractográficas e micrográficas das regiões de iniciação das fraturas foram realizadas por microscopia eletrônica de varredura. A variação dos micromecanismos de iniciação em função da variação da capacidade plástica local na raiz dos entalhes, como induzida pela variação da temperatura de ensaio e pela variação do raio da raiz, foi analisada. De um modo geral, três tipos de micromecanismos de iniciação foram observados. Um frágil, em que a iniciação envolve a nucleação de uma microtrinca à frente do entalhe e sua subsequente propagação instável. Dois dúcteis, um pela ruptura por cisalhamento localizado ao longo de linhas de cisalhamento máximo formadas na raiz do entalhe, e outro pela formação de microcavidades cuja ligação entre si e a ponta do entalhe envolve um processo misto de cisalhamento localizado e de coalescência de microcavidades. Aspectos de modelos que relacionam tenacidade com a microestrutura foram discutidos com base nos micromecanismos observados. / In this study a detailed analysis of the micromechanisms of the fracture initiation in notched specimens was made, for five steels and two aluminum alloys. With that purpose brittle/ductile transition and fracture toughness x r1/2 curves were obtained, and interrupted tests before the fracture of the sample were used. Fractographic and micrographic analysis of the fracture initiation areas were accomplished by scanning electron microscopy. The variation of the initiation micromechanisms in function of the variation of the local plastic capacity in the notch root, as induced by the variation of the test temperature and by the variation of the notch root radius, was analyzed. In a general way, three types of initiation micromechanisms were observed. A brittle one, where the initiation involves the microcrack nucleation ahead of the notch and its subsequent unstable propagation. Two ductile, one by localized shear rupture along the maximum shear lines formed in the notch root, and other by microvoids nucleation whose link to each other and the notch tip involves a mixed process of localized shear and microcavoid coalescence. Aspects of relating models of fracture toughness with microstructure were discussed, based in the observed micromechanisms.

Resumo: Neste trabalho foi feita uma análise detalhada dos micromecanismos de iniciação da fratura em amostras entalhadas para cinco aços e duas ligas de alumínio. Com esse objetivo foram obtidas curvas de transição frágil-dúctil e de tenacidade à fratura em função do raio da raiz do entalhe, e realizados ensaios interrompidos antes da fratura da amostra. Análises fractográficas e micrográficas das regiões de iniciação das fraturas foram realizadas por microscopia eletrônica de varredura. A variação dos micromecanismos de iniciação em função da variação da capacidade plástica local na raiz dos entalhes, como induzida pela variação da temperatura de ensaio e pela variação do raio da raiz, foi analisada. De um modo geral, três tipos de micromecanismos de iniciação foram observados. Um frágil, em que a iniciação envolve a nucleação de uma microtrinca à frente do entalhe e sua subsequente propagação instável. Dois dúcteis, um pela ruptura por cisalhamento localizado ao longo de linhas de cisalhamento máximo formadas na raiz do entalhe, e outro pela formação de microcavidades cuja ligação entre si e a ponta do entalhe envolve um processo misto de cisalhamento localizado e de coalescência de microcavidades. Aspectos de modelos que relacionam tenacidade com a microestrutura foram discutidos com base nos micromecanismos observados. / Abstract: In this study a detailed analysis of the micromechanisms of the fracture initiation in notched specimens was made, for five steels and two aluminum alloys. With that purpose brittle/ductile transition and fracture toughness x r1/2 curves were obtained, and interrupted tests before the fracture of the sample were used. Fractographic and micrographic analysis of the fracture initiation areas were accomplished by scanning electron microscopy. The variation of the initiation micromechanisms in function of the variation of the local plastic capacity in the notch root, as induced by the variation of the test temperature and by the variation of the notch root radius, was analyzed. In a general way, three types of initiation micromechanisms were observed. A brittle one, where the initiation involves the microcrack nucleation ahead of the notch and its subsequent unstable propagation. Two ductile, one by localized shear rupture along the maximum shear lines formed in the notch root, and other by microvoids nucleation whose link to each other and the notch tip involves a mixed process of localized shear and microcavoid coalescence. Aspects of relating models of fracture toughness with microstructure were discussed, based in the observed micromechanisms. / Orientador: Fathi Aref Ibrahim Darwish / Coorientador: Luís Rogério de Oliveira Hein / Banca: Valdir Alves Guimarães / Banca: Marcelo dos Santos Pereira / Banca: Luiz Carlos Pereira / Banca: Marcos Venicius Soares Pereira / Doutor

Bistable microrelays have many possible applications and have the potential to reduce the size, weight, power consumption, and cost of products in which they are used. This research outlines the current state of microrelays, presents three new compliant bistable micromechanisms, and characterizes their performance as microrelays. The characterization includes a treatment of a new force-tester, a preliminary contact resistance study, contact-force measurements, switching time measurements, insertion loss, AC isolation, breakdown voltage, and DC isolation. This document also includes recommendations for further research.

The purpose of this research is to present a class of Self-Retracting Fully-compliant Bistable Micromechanisms (SRFBM). Fully-compliant mechanisms are needed to overcome the inherent limitations of microfabricated pin joints, especially in bistable mechanisms. The elimination of the clearances associated with pin joints will allow more efficient bistable mechanisms with smaller travel. Small travel, in a linear path facilitates integration with efficient on-chip actuators. Tensural pivots are developed and used to deal with the compressive loading to which the mechanism is subject. SRFBM are modeled using the Pseudo-Rigid-Body Model and finite element analysis. Suitable configurations of the SRFBM concept have been identified and fabricated using the MUMPs process. Complete systems, including external actuators and electrical contacts are 1140 μm by 625 μm (individual SRFBM are less than 300 μm by 300 μm). These systems have been tested, demonstrating on-chip actuation of bistable mechanisms. Power requirements for these systems are approximately 150 mW. Testing with manual force testers has also been completed and correlates well with finite element modeling. Actuation force is approximately 500 μN for forward actuation. Return actuation can be achieved either by external actuators or by thermal self-retraction of the mechanism. Thermal self-retraction is more efficient, but can result in damage to the mechanism. Fatigue testing has been completed on a single device, subjecting it to approximately 2 million duty cycles without failure. Based on the SRFBM concept a number of improvements and adaptations are presented, including systems with further power and displacement reductions and a G-switch for LIGA fabrication.

Compliant bistable micromechanisms have been proposed for use in applications such as switches, relays, shutters, and sensing arrays. Unpublished laboratory testing suggests that off-axis forces may affect the bistable nature of fully compliant bistable micromechanisms (FCBMs). The actuation forces required to snap the FCBM from one stable equilibrium position to another can be altered if the off-axis forces are applied to the mechanism during transition between stable positions. Understanding the three-dimensional characteristics of these mechanisms and the effect of eccentric loading conditions would be helpful in design and analysis of FCBMs. Two 3-D FEA models were developed for analysis and validation purposes. The 3-D solid element model includes great detail regarding the geometry and boundary conditions of the FCBMs. Including fillets, residual stress, and anchors proved to generate more accurate results. The 3-D beam element model is greatly simplified, and primarily used to validate the results produced by the 3-D solid element model. Both models were validated through comparison to experimental data. A test suite of FEA runs was constructed to better understand the 3-D behavior of FCBMs. A chief discovery provided by the test suite results was the existence of two phenomenon conditions, defined as Phenomenon 1 and Phenomenon 2. Phenomenon 1 tended to occur when smaller off-axis forces were included in the model. When comparing the two phenomenon, larger pitch rotation, smaller out-of-plane motion, larger reaction forces, and a more consistent bistable mechanism was associated with Phenomenon 1. Phenomenon 2 tended to occur when larger applied forces were included in the model. Once this phenomenon was generated, the FCBM tended to remain in this condition. Reduced reaction forces, larger out-of-plane motion, and a tendency of non-bistability were characteristics of this phenomenon. The FCBMs could experience much larger in-plane applied forces before transitioning to Phenomenon 2. In contrast, relatively small out-of-plane forces caused the same transition. The FCBMs proved to be well behaved when being pulled into their alternate stable position rather than being pushed. A pushing motion caused the shuttle to roll, pitch and yaw in an inconsistent manner.

Neste trabalho, foi investigado o efeito do tamanho do abrasivo na resistência ao desgaste de cinco ligas metálicas. Foi usado, para este estudo, o equipamento pino contra lixa e alumina como abrasivo, com tamanho médio entre 16 µm e 192 µm. A microestrutura das ligas metálicas foi caracterizada com microscopia ótica e os mecanismos de desgaste abrasivo e os microcavacos (partículas de desgaste) foram caracterizados usando microscopia eletrônica de varredura (MEV). Em uma primeira série de experimentos, foi usado ferro fundido mesclado com carbonetos M3C (temperado e revenido a temperaturas entre 300 e 600°C). Para abrasivos pequenos, a perda de massa elevou-se com o aumento do tamanho do abrasivo. Entretanto, para abrasivos grandes, a perda de massa aumenta com inclinação menor e o mecanismo prevalente de desgaste é o microcorte. Para abrasivos maiores, o mecanismo prevalente de desgaste é microsulcamento. Em uma segunda série de experimentos, foi usado ferro fundido branco (FFB), com matrizes austenítica e martensítica. O FFB com matriz austenítica apresentou um tamanho crítico de abrasivo (TCA) de 36 µm e, para o ferro fundido martensítico, foi aproximadamente de 116 µm. A perda de massa do ferro fundido com matriz austenítica aumentou linearmente com o aumento do tamanho dos abrasivos, após o TCA a perda de massa aumenta com inclinação menor. O FFB martensítico, com menores tamanhos do abrasivo, apresentou um comportamento linear. Existe, porém, uma região de transição não-linear e achatada, quando o tamanho de partícula crítico é atingido, tornando-se independente do tamanho do abrasivo. Antes do TCA, o micromecanismo prevalente de desgaste foi microcorte e a lixa apresentou cavacos contínuos e finos e, após o TCA, o mecanismo prevalente de desgaste foi microsulcamento e apresentou cavacos descontínuos e deformados. O efeito do tamanho de abrasivo observado na perda de massa foi apresentado na energia especifica de corte e no coeficiente de atrito. Em uma terceira série de experimentos, foi usado alumínio e aço AISI 1045. O alumínio (estrutura cristalina cúbica de fase centrada) apresentou um comportamento similar ao observado no FFB com matriz austenítica, e o aço AISI 1045 apresentou um comportamento similar ao FFB com matriz martensítica. Verificou-se que, no alumínio e no aço AISI 1045, também se apresenta mudança na morfologia dos cavacos e nos micromecanismos de desgaste, observados nos materiais com segunda fase dura. Em uma quarta série de experimentos, foi usado o ferro fundido cinzento para corroborar a mudança dos micromecanismos de desgaste abrasivo e dos microcavacos com o TCA. O ferro fundido cinzento não apresentou uma transição (TCA) na curva de tamanho de abrasivo contra perda de massa. A morfologia dos cavacos foi similar para os diferentes tamanhos de abrasivos (descontínua). Para abrasivos menores, porém, apresentaram-se alguns cavacos contínuos e finos. O micromecanismo prevalente de desgaste abrasivo foi de microcorte para os diferentes abrasivos usados. Portanto, nesta pesquisa, foi demonstrado que o tamanho crítico de abrasivo está relacionado com os micromecanismos de desgaste e com a morfologia dos microcavacos. / In this research, the effect of abrasive size on the wear resistance of five metallic materials was investigated. Abrasive wear tests using a pin test on alumina paper were carried out using abrasive sizes between 16 µm and 192 µm. The wear surface of the specimens was examined by scanning electron microscopy for identifying the wear micromechanism and the type of microchips formed on the abrasive paper (wear debris). In a first series of experiments mottled cast iron samples with M 3 C carbides were tested. The samples were quenched and tempered in temperatures ranging from 300°C to 600°C. For small abrasive particles, the wear mass loss increased linearly with the increase of particle size. However, for higher abrasive sizes the wear mass loss increased much more slowly. For lower abrasive sizes the main wear mechanism was microcutting. For higher abrasive sizes, the main wear mechanism was microploughing. In a second series of experiments white cast iron with M 3 C carbide with austenitic and martensitic matrix were tested. The results show that the mass loss for cast irons with austenitic and martensitic matrices increases linearly with the increase of particle size until the critical particle size is reached. The cast iron with austenitic matrix presented a critical abrasive size of 36 µm and for the martensitic cast iron, the critical particle size was about 116 µm. After the critical particle size is reached, the rate of mass loss of the cast iron with austenitic matrix diminishes to a lower linear rate, and for cast irons with martensitic matrix the curve of mass loss is non-linear and flattens when the critical particle size is reached. It becomes, then, constant, independent of additional size increases. The abrasive paper in contact with the iron of both austenitic and martensitic matrices presents fine continuous microchips and the main wear mechanism was microcutting before reaching critical particle size, and after that it presents deformed discontinuous microchips and the main wear mechanism was microploughing. This behavior of change in rates after reaching a critical size happened not only for mass loss versus abrasive size, but it was also observed both in curves of friction coefficient and specific cutting energy versus abrasive size. In a third series of experiments aluminum and AISI 1045 steel were tested. The first (FCC structure) showed similar behavior to that observed in the white cast iron with austenitic matrix and the latter showed similar behavior to that observed in white cast iron with martensitic matrix. Both aluminum and AISI 1045 steel show similar changes in the microchips morphology and in the wear micromechanisms, something that had been observed before in materials with hard second phase. In a fourth series of experiments gray cast iron was tested in order to demonstrate the relationship between the abrasive wear micromechanisms and the type of microchips, before and after achieving critical abrasive size. The grey cast iron did not show a transition in the curve of abrasive size against mass loss. The morphology of the chips was similar for the different sizes of abrasive (discontinuous). However, smaller abrasive sizes some thin continuous microchips were formed. The main abrasive wear micromechanism was microcutting for the different abrasives sizes tested. Therefore, it was shown that the critical abrasive size is related to the wear micromechanisms and the microchips morphology.

Neste trabalho, foi investigado o efeito do tamanho do abrasivo na resistência ao desgaste de cinco ligas metálicas. Foi usado, para este estudo, o equipamento pino contra lixa e alumina como abrasivo, com tamanho médio entre 16 µm e 192 µm. A microestrutura das ligas metálicas foi caracterizada com microscopia ótica e os mecanismos de desgaste abrasivo e os microcavacos (partículas de desgaste) foram caracterizados usando microscopia eletrônica de varredura (MEV). Em uma primeira série de experimentos, foi usado ferro fundido mesclado com carbonetos M3C (temperado e revenido a temperaturas entre 300 e 600°C). Para abrasivos pequenos, a perda de massa elevou-se com o aumento do tamanho do abrasivo. Entretanto, para abrasivos grandes, a perda de massa aumenta com inclinação menor e o mecanismo prevalente de desgaste é o microcorte. Para abrasivos maiores, o mecanismo prevalente de desgaste é microsulcamento. Em uma segunda série de experimentos, foi usado ferro fundido branco (FFB), com matrizes austenítica e martensítica. O FFB com matriz austenítica apresentou um tamanho crítico de abrasivo (TCA) de 36 µm e, para o ferro fundido martensítico, foi aproximadamente de 116 µm. A perda de massa do ferro fundido com matriz austenítica aumentou linearmente com o aumento do tamanho dos abrasivos, após o TCA a perda de massa aumenta com inclinação menor. O FFB martensítico, com menores tamanhos do abrasivo, apresentou um comportamento linear. Existe, porém, uma região de transição não-linear e achatada, quando o tamanho de partícula crítico é atingido, tornando-se independente do tamanho do abrasivo. Antes do TCA, o micromecanismo prevalente de desgaste foi microcorte e a lixa apresentou cavacos contínuos e finos e, após o TCA, o mecanismo prevalente de desgaste foi microsulcamento e apresentou cavacos descontínuos e deformados. O efeito do tamanho de abrasivo observado na perda de massa foi apresentado na energia especifica de corte e no coeficiente de atrito. Em uma terceira série de experimentos, foi usado alumínio e aço AISI 1045. O alumínio (estrutura cristalina cúbica de fase centrada) apresentou um comportamento similar ao observado no FFB com matriz austenítica, e o aço AISI 1045 apresentou um comportamento similar ao FFB com matriz martensítica. Verificou-se que, no alumínio e no aço AISI 1045, também se apresenta mudança na morfologia dos cavacos e nos micromecanismos de desgaste, observados nos materiais com segunda fase dura. Em uma quarta série de experimentos, foi usado o ferro fundido cinzento para corroborar a mudança dos micromecanismos de desgaste abrasivo e dos microcavacos com o TCA. O ferro fundido cinzento não apresentou uma transição (TCA) na curva de tamanho de abrasivo contra perda de massa. A morfologia dos cavacos foi similar para os diferentes tamanhos de abrasivos (descontínua). Para abrasivos menores, porém, apresentaram-se alguns cavacos contínuos e finos. O micromecanismo prevalente de desgaste abrasivo foi de microcorte para os diferentes abrasivos usados. Portanto, nesta pesquisa, foi demonstrado que o tamanho crítico de abrasivo está relacionado com os micromecanismos de desgaste e com a morfologia dos microcavacos. / In this research, the effect of abrasive size on the wear resistance of five metallic materials was investigated. Abrasive wear tests using a pin test on alumina paper were carried out using abrasive sizes between 16 µm and 192 µm. The wear surface of the specimens was examined by scanning electron microscopy for identifying the wear micromechanism and the type of microchips formed on the abrasive paper (wear debris). In a first series of experiments mottled cast iron samples with M 3 C carbides were tested. The samples were quenched and tempered in temperatures ranging from 300°C to 600°C. For small abrasive particles, the wear mass loss increased linearly with the increase of particle size. However, for higher abrasive sizes the wear mass loss increased much more slowly. For lower abrasive sizes the main wear mechanism was microcutting. For higher abrasive sizes, the main wear mechanism was microploughing. In a second series of experiments white cast iron with M 3 C carbide with austenitic and martensitic matrix were tested. The results show that the mass loss for cast irons with austenitic and martensitic matrices increases linearly with the increase of particle size until the critical particle size is reached. The cast iron with austenitic matrix presented a critical abrasive size of 36 µm and for the martensitic cast iron, the critical particle size was about 116 µm. After the critical particle size is reached, the rate of mass loss of the cast iron with austenitic matrix diminishes to a lower linear rate, and for cast irons with martensitic matrix the curve of mass loss is non-linear and flattens when the critical particle size is reached. It becomes, then, constant, independent of additional size increases. The abrasive paper in contact with the iron of both austenitic and martensitic matrices presents fine continuous microchips and the main wear mechanism was microcutting before reaching critical particle size, and after that it presents deformed discontinuous microchips and the main wear mechanism was microploughing. This behavior of change in rates after reaching a critical size happened not only for mass loss versus abrasive size, but it was also observed both in curves of friction coefficient and specific cutting energy versus abrasive size. In a third series of experiments aluminum and AISI 1045 steel were tested. The first (FCC structure) showed similar behavior to that observed in the white cast iron with austenitic matrix and the latter showed similar behavior to that observed in white cast iron with martensitic matrix. Both aluminum and AISI 1045 steel show similar changes in the microchips morphology and in the wear micromechanisms, something that had been observed before in materials with hard second phase. In a fourth series of experiments gray cast iron was tested in order to demonstrate the relationship between the abrasive wear micromechanisms and the type of microchips, before and after achieving critical abrasive size. The grey cast iron did not show a transition in the curve of abrasive size against mass loss. The morphology of the chips was similar for the different sizes of abrasive (discontinuous). However, smaller abrasive sizes some thin continuous microchips were formed. The main abrasive wear micromechanism was microcutting for the different abrasives sizes tested. Therefore, it was shown that the critical abrasive size is related to the wear micromechanisms and the microchips morphology.

Microactuators are needed to convert energy into mechanical work at the microscale. Thermal microactuators can be used to produce this needed mechanical work. The purpose of this research was to design, fabricate, and test thermal microactuators for use at the microscale in microelectromechanical systems (MEMS). The microactuators developed were tested to determine the magnitude of their deflection and estimate their force. Five groups of thermal microactuators were designed and tested. All of the groups used the geometrically constrained expansion of various segments to produce their deflection. The first group, Thermal Expansion Devices (TEDs), produced a rotational displacement and had deflections up to 20 µm. The second group, Bi-directional Thermal Expansion Devices (Bi-TEDs) were similar to the TEDs. The difference, as the name implies, was that the Bi-TEDs deflected up to 6 µm in two directions. Thermomechanical In-plane Micromechanisms (TIMs) were the third group tested. They produced a linear motion up to 20 µm. The fourth group was the Rapid Expansion Bi-directional Actuators (REBAs). These microactuators were bi-directional and produced up to 12 µm deflection in each direction. The final group of thermal microactuators was the Joint Actuating Micro-mechanical Expansion Systems (JAMESs). These thermal microactuators rotated pin joints up to 8 degrees. The thermal microactuators studied can be used in a wide variety of applications. They can move ratchets, position valves, move switches, change devices, or make connections. The thermal microactuator groups have their own unique advantages. The TIMS can be tailored for the amount of deflection and output force they produce. This will allow them to replace some microactuator arrays and decrease the space used for actuation. The Bi-TEDs and REBAs are bi-directional and can possibly replace two single direction micro-actuators. The JAMESs can be attached directly to a pin joint of an existing mechanism. These advantages allow these thermal microactuator groups to be used for a wide variety of applications.

Devido à fragilidade do concreto, o controle e combate da fissuração são de importância fundamental em estruturas de concreto armado. Uma maneira de melhorar as propriedades do concreto à tração é pelo emprego de fibras. A presente pesquisa é uma tentativa de fornecer diretrizes para o dimensionamento de estruturas de concreto armado com fibras, e armadura convencional sob condições de serviço. Apresenta-se inicialmente, um estudo do comportamento do material à tração. Um modelo probabilístico/micro-mecânico fundamentado na mecânica de fratura, e capaz de prever o comportamento pós-fissuração do compósito é apresentado. O modelo prevê a relação tensão-abertura de fissura do compósito levando em conta os seguintes micro-mecanismos: travejamento de agregado e fibras, a ruptura das fibras, os efeitos de: atrito local (snubbing effect), esmagamento da matriz, Cook-Gordon, e da pré-tração das fibras. Em nível estrutural, dois modelos macro-mecânicos são apresentados. O primeiro modelo tem premissa na teoria clássica de fissura, e o segundo na mecânica de dado. O primeiro modelo é ajustado para aplicação na previsão de espaçamento e aberturas de fissura em estruturas de concreto armado com fibras discretas e aleatoriamente dispostas. É demostrado que o modelo micro-mecânico pode alimentar perfeitamente o modelo macro-mecânico. Ensaios de tração com elementos de placas de argamassa com fibras armada com tela ou fios foram realizados. Os resultados teóricos previstos pelo modelo foram comparados com os obtidos do programa experimental, e mostram uma boa concordância, comprovando a validade do modelo apresentado. / Due to the brittleness of concrete, the control and prevention of cracking in reinforced concrete structures are of prime importance. One way of improving the tensile properties of concrete is by the addition of fibres. The present research is a trial to provide guidelines for the design of fibre reinforced concrete structures under service loads. First of all, a study of the tensile behaviour of the composite material is presented. A probabilistic/fracture mechanics based micromechanical model, capable of predicting the poscracking behaviour of the material is presented. The model predicts the tensile stress-crack width relationship, accounting for the following micromechanisms: fibre and aggregate bridging, fibre rupture, local snubbing, matrix spalling, the Cook-Gordon interface effect, and fibre prestressing. At the structural level, two macromechanical models are presented. One is founded on the classical theory of cracking, while the other, a shear lag model, is founded on the continuum damage mechanics. The first model is adjusted for application to the prevision of crack width and crack spacing in fibre reinforced concrete structures with short discrete and randomly dispersed fibres. It is shown that the micromechanical model fits very well in the macrostructural model. Tensile tests with mortar specimens reinforced with continuous steel wires or meshes and PVA or polypropylene fibres were carried out. The theoretical results predicted by the model were compared with results obtained from the experimental program, and show very good agreement, confirming the validity of the theoretical model.

Devido à fragilidade do concreto, o controle e combate da fissuração são de importância fundamental em estruturas de concreto armado. Uma maneira de melhorar as propriedades do concreto à tração é pelo emprego de fibras. A presente pesquisa é uma tentativa de fornecer diretrizes para o dimensionamento de estruturas de concreto armado com fibras, e armadura convencional sob condições de serviço. Apresenta-se inicialmente, um estudo do comportamento do material à tração. Um modelo probabilístico/micro-mecânico fundamentado na mecânica de fratura, e capaz de prever o comportamento pós-fissuração do compósito é apresentado. O modelo prevê a relação tensão-abertura de fissura do compósito levando em conta os seguintes micro-mecanismos: travejamento de agregado e fibras, a ruptura das fibras, os efeitos de: atrito local (snubbing effect), esmagamento da matriz, Cook-Gordon, e da pré-tração das fibras. Em nível estrutural, dois modelos macro-mecânicos são apresentados. O primeiro modelo tem premissa na teoria clássica de fissura, e o segundo na mecânica de dado. O primeiro modelo é ajustado para aplicação na previsão de espaçamento e aberturas de fissura em estruturas de concreto armado com fibras discretas e aleatoriamente dispostas. É demostrado que o modelo micro-mecânico pode alimentar perfeitamente o modelo macro-mecânico. Ensaios de tração com elementos de placas de argamassa com fibras armada com tela ou fios foram realizados. Os resultados teóricos previstos pelo modelo foram comparados com os obtidos do programa experimental, e mostram uma boa concordância, comprovando a validade do modelo apresentado. / Due to the brittleness of concrete, the control and prevention of cracking in reinforced concrete structures are of prime importance. One way of improving the tensile properties of concrete is by the addition of fibres. The present research is a trial to provide guidelines for the design of fibre reinforced concrete structures under service loads. First of all, a study of the tensile behaviour of the composite material is presented. A probabilistic/fracture mechanics based micromechanical model, capable of predicting the poscracking behaviour of the material is presented. The model predicts the tensile stress-crack width relationship, accounting for the following micromechanisms: fibre and aggregate bridging, fibre rupture, local snubbing, matrix spalling, the Cook-Gordon interface effect, and fibre prestressing. At the structural level, two macromechanical models are presented. One is founded on the classical theory of cracking, while the other, a shear lag model, is founded on the continuum damage mechanics. The first model is adjusted for application to the prevision of crack width and crack spacing in fibre reinforced concrete structures with short discrete and randomly dispersed fibres. It is shown that the micromechanical model fits very well in the macrostructural model. Tensile tests with mortar specimens reinforced with continuous steel wires or meshes and PVA or polypropylene fibres were carried out. The theoretical results predicted by the model were compared with results obtained from the experimental program, and show very good agreement, confirming the validity of the theoretical model.