Ao longo dos anos o crescente interesse pelo aumento das propriedades mecânicas de resistência dos aços, bem como busca por uma tenacidade à fratura aumentada, tem levado o desenvolvimento de novos aços de ultra-alta resistência. Essa classe de aços se demonstra bastante adequada a uma série de aplicações em componentes de alta responsabilidade, como os da indústria aeronáutica. O aço VART 100 é um desenvolvimento da Villares Metals S.A. e é um aço diferenciado, por seu maior teor de níquel, cromo e molibdênio e pela introdução de cobalto em sua composição química que se apresenta como um aço nacional para substituição com vantagens do aço SAE 300M. No mercado internacional existe um aço que tem sido utilizado para este tipo de aplicação com grande sucesso que é o aço AerMet 100. Vários ciclos de tratamentos térmicos podem ser utilizados no VART 100 levando a uma elevada resistência mecânica que pode ter sérias implicações na sua tenacidade à fratura e resistência a fadiga. Este trabalho faz parte de um estudo maior do aço VART100, onde as propriedades mecânicas de tenacidade ao impacto, tenacidade à fratura, vida em fadiga e resistência a propagação de trinca por fadiga estão sendo estudados. Especificamente neste trabalho foram realizadas analises microestruturais, ensaios de dureza Rockwell, ensaios de tração, propagação de trinca por fadiga, curvas da/dN x ΔK e de tenacidade à fratura,KIC, além da avaliação dos micromecanismos de fratura. Os resultados da análise microestrutural mostrou que os grãos da austenita anterior possuem um tamanho médio de 11,6 μm e uma distribuição homogênea de finos precipitados na matriz de martensita envelhecida. Os parâmetros de resistência mecânica obtidos no ensaio de tração do aço VART 100 se apresentaram muito similares aos dos aços SAE 300M e AerMet 100, entretanto os parâmetros de ductilidade apresentaram valores superiores em relação tanto ao 300M quanto em relação ao Aermet 100. Do ensaio de tenacidade à fratura, observa-se que em relação ao aço SAE 300M, o aço VART 100 apresenta uma superior tenacidade à fratura, entretanto com relação ao AerMet 100, ainda que os parâmetros de resistência são similares, o AerMet 100 apresenta uma destacada superioridade na tenacidade à fratura (cerca de 57% superior). Dos parâmetros obtidos nos ensaios de propagação de trinca por fadiga, observamos que os valores de ΔK0 da Região I são semelhantes independente das direções ensaiadas R-C e LR, mas há uma pequena redução nesse valor quando a razão de carga aumentou de 0,1 para 0,5. A região de Paris foi insensível a variação da razão de carga. Assim, os parâmetros C e m obtidos na Região II, fornece valores bastante similares, que comparados através da utilização da equação de Forman modificada, nos permite notar um desempenho levemente superior do Aermet 100 comparado ao VART 100. / Over the years a growing interest in increasing the mechanical strength of steels, as well as, the search for an increased fracture toughness, has led to the development of new ultra-high resistance steels. This class of steels demonstrated to be well suited to a variety of applications in components of high responsibility, such as the ones for the aerospace industry. The VART 100 steel is a Villares Metals S.A. development and is a distinctive steel, for its higher content of nickel, chromium and molybdenum and the introduction of cobalt and Ti in its chemical composition that presents as a national option for replacement, with advantages, for the SAE 300M steel . In the international market there is a steel that has been used for this type of application with great success, it is named AerMet 100. Different heat treatment cycles can be used in VART 100 leading to high mechanical resistance that may cause serious implications on their fracture toughness and fatigue resistance. This work is part of a larger study with the VART100 steel, where the mechanical properties, such as impact resistance, fracture toughness, fatigue life, and fatigue crack propagation resistance are being studied. Specifically in this work the microstructural analysis, Rockwell hardness testing, tensile, fatigue crack propagation curves da / dN x ΔK and fracture toughness, KIC, were carried out. The microstructural results showed that the prior austenite grains have an average size of 11.6 μm and a homogeneous distribution of fine precipitates in a aged martensite matrix. The mechanical strength obtained in the tensile test of the VART 100 steel are very similar to both the SAE 300M steels and AerMet 100, however the ductility parameters showed higher values than the ones for 300M and Aermet 100 steels. From the fracture toughness test, it was observed that the VART 100 exhibits superior fracture toughness than the SAE 300M, but in relation to the AerMet 100 steel, although the strength parameters are similar, the AerMet 100 presented an outstanding superior fracture toughness (about 57% higher). From the fatigue crack propagation tests, we observed that the values of K0 (Region I) are similar regardless of the tested R-C and L-R directions, but there is a small reduction in value when the load ratio increased from 0.1 to 0.5 . The Paris region was insensitive to variation of the load ratio. Thus, the C and m parameters, obtained in Region II, provided very similar values, if compared by using the modified Forman equation, allows us to observe a slightly higher performance of AerMet 100 when compared to VART 100.

<div>Self-pierce riveting as a relative new technology has been used by automotive industry for decades. Because of the several benefits of the SPR technique, it has been widely used for joining the similar or dissimilar materials to satisfy the light-weighting requirements of automobile. There were many researchers and automotive manufacturers that had been investigated the SPR by experiments and applied this technique to their products. The SPR was designed for joining the materials with sufficient ductility because the joining process was going to introduce the large plastic deformation on the joint button area. Die casting aluminum alloy products became more and more popular to be used for structural components. However, the casting aluminum components have relative low ductility than the wrought alloy product. The cracking problems were easy to occur during the riveting process.</div><div><br></div><div>In terms of the cracking issues on die casting aluminum products, an analysis was conducted in this study to investigate the influence of composition on cracking problem. And the cracking mechanism was also analyzed and summarized. Corresponding to the influence of silicon content difference and silicon morphology, heat treatment was used to modify the eutectic silicon morphology of the casting aluminum alloys to improve the rivetability. Once the silicon network was broken by the heat treatment, the rivetability of die casting aluminum was drastically increased and the cracks on joint button were also suppressed. Under the effect of heat treatment, the joint performance was tightly related to the variation of the eutectic silicon phase and the cracks on the joint button. The joint strength was obtained by shear test to investigate the influence of heat treatment and die depth. A novel cracking statistics has been generated and used to calculate the cracks on the joint button. Eventually, a comprehensive joint performance was obtained by taking into consideration of joint strength, heat treatment and die depth.</div><div><br></div><div>Finally, the simulation of the SPR process was conducted and analyzed by FORGE. The die depth as the variable was used to investigate the strain and fracture distribution in</div><div>cross-section view of the joint. In terms of the initial results of the simulation, the die cavity with various sidewall incline angles was simulated to find the optimal die cavity geometry in order to improve the rivetability of the bottom material sheet.</div>

An experimental investigation was undertaken to determine the effects of marine environmental exposure on the mechanical properties of vinylester resins (VE510A and VE8084) and carbon fiber/VE510A vinylester composites. The effect of carbon fiber sizing on the composite strengths was also examined. Neat resins were exposed to marine environments until moisture content reached a point of saturation after which they were tested in tension, compression and shear. Compared to the baseline dry specimens, specimens subjected to moisture showed overall increased ductility and a reduction in strength. Dry and moisture saturated composite specimens were tested in tension and compression in different orientations. Longitudinal specimens were tested in in-plane shear and interlaminar shear. Composites with F-sized carbon fibers displayed overall higher strength than those with G-sized fibers at both dry and moisture saturated conditions. An analysis of moisture absorption of the composites was performed which vii shows that the moisture up-take is dominated by the fiber/matrix region which absorbs up to 90% of the moisture. The composites experienced reduced strength after moisture absorption. The results revealed that the fiber sizing has stronger effect on the fiber/matrix interface dominated strengths than moisture up-take. / by Alexander M. Figlionini. / Thesis (M.S.C.S.)--Florida Atlantic University, 2011. / Includes bibliography. / Electronic reproduction. Boca Raton, Fla., 2011. Mode of access: World Wide Web.

Durability of the composite materials in marine environments has been investigated experimentally and with analytical and numerical methods. The main focus of this study is on the integrity of the fiber/matrix interface under seawater exposure. A single-fiber compression test specimen called the Outwater-Murphy (OM) test has been analyzed using mechanics of materials principles and linear elastic fracture mechanics. Sizing of the OM specimen was conducted so that debonding of the fiber from the interface should be achieved prior to yielding of the matrix and global instability failure. Stress analysis of the OM specimen has been conducted from theory of elasticity and finite element analysis. A superelement technique was developed for detailed analysis of the stress state at the fiber/matrix interface. The interface stress state at the debond site in the OM specimen, i.e. at the hole edge, was identified as biaxial tension at the fiber/matrix interface. Characterization of cure and post-cure of 8084 and 510A vinlyester resins has been performed using cure shrinkage tests based on dynamic mechanical analysis and coated beam experiments. In addition, moisture absorption, swelling and the influence of moisture on the mechanical properties of the resins were determined. Testing of OM specimens consisting of a single carbon or glass fiber embedded in vinylester resin at dry conditions and after seawater exposure revealed that the debond toughness was substantially reduced after exposure of the OM specimen to seawater. C(F) did not debond. Macroscopic carbon/vinylester woven composites where the fibers were sized with F sizing were tested in shear at dry conditions and after four weeks of seawater exposure. The shear strength was very little affected after the short immersion time. / by Muhammad Umar Farooq. / Thesis (Ph.D.)--Florida Atlantic University, 2009. / Includes bibliography. / Electronic reproduction. Boca Raton, Fla., 2009. Mode of access: World Wide Web.

In this investigation, polymer precursor of syntactic foam has been reinforced with SiC nanoparticles to enhance mechanical and fracture properties. Derakane 8084 vinyl ester resin was first dispersed with 1.0 wt% of SiC particles using a sonic cavitation technique. In the next step, 30.0 wt% of microspheres (3M hollow glass borosilicate, S-series) were mechanically mixed with the nanophased vinyl ester resin, and cast into rectangular molds. A small amount of styrene was used as dilutant to facilitate mixing of microspheres. The size of microspheres and SiC nanoparticles were 20-30 um and 30-50 nm, respectively. Tension, compression, and flexure tests were conducted following ASTM standards and a consistent improvement in strength and modulus within 20-35% range was observed. Fracture toughness parameters such as KIC and GIC were also determined using ASTM E-399. An improvement of about 11-15% was observed. Samples were also subjected to various environmental conditions and degradation in material properties is reported. / by Debdutta Das. / Thesis (M.S.C.S.)--Florida Atlantic University, 2009. / Includes bibliography. / Electronic reproduction. Boca Raton, Fla., 2009. Mode of access: World Wide Web.

Additive manufacturing (AM) is a novel near-net-shape manufacturing technology which deposited a component layer by layer directly from 3D CAD files. This rapid and complex weld pool process may introduce short and long range microstructure heterogeneities, which can potentially impact on the local mechanical properties of AM components. The present research thus focuses on the quantitatively analysing the microstructural heterogeneity, by the development and application of methods for the SEBM and WAAM Ti-6Al-4V parts. An additive manufacturing microstructure quantification tool, 'AMMQ', has been developed that combines automatic high resolution SEM image mapping with batch image analysis, to enable efficient quantification over large areas at the required resolution. It was found that the microstructural variation could be described by two key parameters, namely: the mean alpha plate spacing and mean β circularity of the retained β phase. The former corresponds to the combined effect of the rate of solid-state phase transformation upon cooling through the β transus in the first sub-Tβ thermal cycles followed by coarsening, whereas the latter attributes to a spheroidisation effect during subsequent re-heating and annealing below the β transus. The microstructure analysis algorithms showed adequate consistency for the possible varying imaging conditions, and for the different AM Ti-6Al-4V microstructure morphologies. In the SEBM specimens, a layer-scale periodicity in β phase circularity was detected, and a systematic drift of 'hot/cold regions was seen in the geometric specimens. Numerical modelling using a Rosenthal's model showed that the varied cooling conditions with respect to layer depth could be responsible for the layer-wise heterogeneity. Moreover, it has been shown that there is a direct linkage between thermal input, microstructure, and porosity density, as lack of fusion defects were detected in regions of low heat input, as inferred from local alpha plate measurements. This heterogeneity can firstly attribute to the SEBM control themes which were not optimised. Secondly, the heat dissipation condition for each geometry could also have affected the accumulated heat received for each volume of a part. In the WAAM specimens, a periodic microstructure pattern was consistently seen in the steady-state regions, where three typical microstructure morphologies were present: fine basketweave, colony alpha, and coarse basketweave. Micro-hardness mapping and in-situ tensile strain analysis were performed to investigate the microstructural influence on mechanical properties. It was found that both the hardness distribution and the tensile strain distribution was a function of the microstructural heterogeneity and that thin bands within each deposited layer with a colony alpha morphology appeared to be the main region of weakness within the deposited microstructures. Otherwise, the local hardness and tensile strength varied inversely to the local mean alpha plate spacing as expected. Finally, two important microstructure evolution mechanisms were proposed: i) alpha plate coarsening by the joining of neighbouring β layer as β phase volume fraction increases as the temperature approaches Tβ; ii) formation of the colony alpha by regrowth from a small fraction of alpha remnants at temperatures very close to Tβ.

Hybrides nano /micrométriques de nanotubes de carbone (NTC) greffés sur microparticules d’alumina, microplaques de SiC ou nanoplaquettes de graphène (NPG) ont été utilisés comme renforts multifonctionnelles dans les composites à matrice polymère. Le NTCs utilisés étaient généralement sous forme de six branches symétriques et orthogonales sur microparticules sphériques d'Al2O3, mais d'une ou deux branches alignées verticalement sur les deux côtés de microplaques de SiC et de NPG. L’introduction des structures hybrides dans une matrice époxy permet d’améliorer la dispersion des NTC et l'interaction interfaciale entre les renforts et la matrice. Les propriétés mécaniques des composites ont été fortement améliorées avec une faible concentration de hybrides. La résistance électrique in situ des composites a atteint d’abord à sa valeur maximale et puis diminue avec la présence d'une déformation irréversible. Ce phénomène observé est complètement différent par rapport à ce des composites renforcé par NTC, c’est-à-dire, une augmentation monotone de la résistance jusqu'à leur rupture final. Les propriétés mécaniques et les comportements de self-sensing des composites dependent fortement de l'élancement de NTC de leur organisation et aussi des substrats. L'introduction des hybrides dans les composites renforcés par des fibres longues (verre) a démontré un grand potentiel pour développer des composites multi-échelles. Les études réalisées sur la matrice époxy renforcée par les hybrides bien dispersés avec une faible fraction ont montré des améliorations importantes des propriétés de flexion à 3 points et des propriétés thermo-mécaniques. Les réseaux conducteurs formés par hybrides nano/micrométriques permettent de suivre in situ l'évolution de l’état de dégradation des composites à matrice époxy renforcés par des tissus de verre sous contrainte appliquée. / Nano/micro multiscale hybrids with carbon nanotubes (CNTs) grown on the Al2O3 microparticles, SiC microplates or graphene nanoplatelets (GNPs) could serve as multifunctional reinforcements in the composites. The CNTs generally form into symmetric six-orthogonal branches on the spherical Al2O3, but vertically align on the flat surfaces of the SiC and GNP. The introduction of hybrids into the epoxy matrix endows uniform dispersion of CNTs as well as improved interfacial interaction between the reinforcements and matrix. Significantly enhanced mechanical properties of the composites were achieved at low hybrid concentration. The in situ electrical resistance of the composites initially increases to its maximum value and then begins to decrease with the appearance of irreversible deformation, which is different from the pristine CNTs filled composites only with monotonic increase of the resistance until their catastrophic fracture. The mechanical and self-sensing behaviors of the composites are found to be highly dependent on CNT aspect ratio, organization and the substrates. Besides, the introduction of hybrids into the traditional fiber-reinforced composites shows great promise in development of the high-performance multiscale composites. The epoxy matrix is toughed by the well dispersed hybrids at low fraction, resulting in improved flexural and thermomechancial properties. Besides, the conductive networks provided by the hybrids could be utilized as in situ damage sensors to monitor the damage evolution in the glass fabric/epoxy composite laminates under tensile loading.

by Woo Ka Fai. / Thesis (M.Phil.)--Chinese University of Hong Kong, 1995. / Includes bibliographical references (leaves 61-63). / Abstract --- p.i / Acknowledgment --- p.ii / Contents --- p.iii / Abbreviations --- p.iv / List of Figures --- p.vii / List of Tables --- p.ix / Chapter 1 --- Introduction --- p.1 / Chapter 2. --- Theoretical background / Chapter 2.1 --- Static light scattering for homopolymer --- p.5 / Chapter 2.2 --- Static light scattering for copolymer --- p.16 / Chapter 2.3 --- Dynamic light scattering --- p.19 / Chapter 2.4 --- Modified method for copolymer --- p.28 / Chapter 3. --- Experimental / Chapter 3.1 --- Preparation of PET-PCL --- p.31 / Chapter 3.2 --- Preparation of solution for LLS --- p.31 / Chapter 3.3 --- Refractive index increment measurement --- p.32 / Chapter 3.4 --- Laser light scattering instrumentation --- p.35 / Chapter 4. --- Results and Discussion --- p.36 / Chapter 5. --- Conclusion --- p.60 / Chapter 6. --- References --- p.61

by Cho, King-sum. / Thesis (M.Phil.)--Chinese University of Hong Kong, 1999. / Includes bibliographical references (leaves 108-110). / Text in English; abstracts in English and Chinese. / by Cho, King-sum. / Abstract --- p.i / 摘要 --- p.iii / Acknowledgment --- p.iv / Contents --- p.v / List of figures --- p.x / Chapter 1 --- Introduction --- p.1 / Chapter 1.1 --- Review of non-destructive techniques --- p.2 / Chapter 1.1.1 --- Liquid penetration technique --- p.2 / Chapter 1.1.2 --- Eddy current inspection --- p.2 / Chapter 1.1.3 --- Ultrasonic testing --- p.3 / Chapter 1.1.4 --- Radiography --- p.3 / Chapter 1.1.5 --- Magnetic testing methods --- p.4 / Chapter 1.2 --- Barkhausen emission --- p.4 / Chapter 1.3 --- The development of Barkhausen Emission --- p.5 / Chapter 1.4 --- The advantages of using Barkhausen emission --- p.6 / Figures for chapter1 --- p.8 / Chapter 2 --- Iron-carbon System --- p.9 / Chapter 2.1 --- Iron-iron carbide phase diagram --- p.9 / Chapter 2.2 --- Invariant reactions in the Fe-Fe3C phase diagram --- p.11 / Chapter 2.3 --- Classification of carbon steels --- p.12 / Chapter 2.4 --- Effect of heat treatment on plain-carbon steels --- p.13 / Chapter 2.4.1 --- Annealing and normalizing --- p.14 / Chapter 2.4.2 --- Slow cooling --- p.15 / Chapter 2.5 --- Process of recovery and recrystallization --- p.15 / Chapter 2.5.1 --- Recovery --- p.16 / Chapter 2.5.2 --- Recrystallization --- p.16 / Chapter 2.5.3 --- Grain growth --- p.17 / Figures for chapter2 --- p.18 / Chapter 3 --- Background Theory --- p.23 / Chapter 3.1 --- Ferromagnetism --- p.23 / Chapter 3.1.1 --- Localized moment theory --- p.24 / Chapter 3.1.2 --- Band theory --- p.25 / Chapter 3.1.3 --- Hysteresis loop --- p.25 / Chapter 3.2 --- Domain theory --- p.26 / Chapter 3.2.1 --- Magnetic domain --- p.26 / Chapter 3.2.2 --- Structure of domain wall --- p.27 / Chapter 3.2.3 --- Domain wall motion --- p.29 / Chapter 3.2.4 --- Magnetostatic energy --- p.30 / Chapter 3.2.5 --- Magnetization process --- p.32 / Chapter 3.3 --- Effect of applied stress --- p.33 / Chapter 3.3.1 --- Stress --- p.33 / Chapter 3.3.2 --- Magnetostriction --- p.34 / Chapter 3.3.3 --- Effect of stress on magnetization --- p.34 / Figures for chapter 3 --- p.37 / Chapter 4 --- Instrumentation --- p.39 / Chapter 4.1 --- Introduction --- p.39 / Chapter 4.2 --- Experimental setup for Barkhausen emission --- p.39 / Chapter 4.2.1 --- Magnetizing unit --- p.40 / Chapter 4.2.2 --- Signal detection unit --- p.41 / Chapter 4.2.3 --- Signal processing unit --- p.42 / Chapter 4.3 --- The typical BE profile --- p.42 / Chapter 4.4 --- Specimen treatment --- p.43 / Chapter 4.4.1 --- Optical microscope --- p.43 / Chapter 4.4.2 --- Vickers´ة hardness tester --- p.44 / Chapter 4.4.3 --- Thermal resistance furnace --- p.45 / Chapter 4.4.4 --- Instron loading machine --- p.45 / Figures for chapter4 --- p.47 / Chapter 5 --- Experiments and Results: Evaluation of Carbon Content in Steel --- p.52 / Chapter 5.1 --- Introduction --- p.52 / Chapter 5.2 --- Experiments and results --- p.52 / Chapter 5.3 --- Discussions --- p.53 / Chapter 5.3.1 --- The magnetization process --- p.53 / Chapter 5.3.2 --- The BE profiles 、 --- p.54 / Chapter 5.3.3 --- Hardness --- p.57 / Chapter 5.4 --- Conclusions --- p.57 / Figures for chapter5 --- p.58 / Chapter 6 --- Experiments and Results: The Effects of annealing on Barkhausen Emission in Mild Steel Bars --- p.64 / Chapter 6.1 --- Introduction --- p.64 / Chapter 6.2 --- Experiments --- p.64 / Chapter 6.3 --- Results and discussions --- p.64 / Chapter 6.3.1 --- The mechanical properties --- p.65 / Chapter 6.3.2 --- Grain size --- p.65 / Chapter 6.3.3 --- BE profiles --- p.66 / Chapter 6.4 --- Conclusions --- p.67 / Figures for chapter6 --- p.68 / Chapter 7 --- Experiments and Results: The Effects of Dynamic and Residual Stresses on Barkhausen Emission in Annealed Mild Steel Bars --- p.76 / Chapter 7.1 --- Introduction --- p.76 / Chapter 7.2 --- Experiments --- p.76 / Chapter 7.2.1 --- Measurement of dynamic loading (with samples of Set A) --- p.77 / Chapter 7.2.2 --- Measurement of residual stress (with samples of Set B) --- p.77 / Chapter 7.2.3 --- Measurement of continuous tensile stress (with samples of Set C) --- p.77 / Chapter 7.3 --- Results and discussions --- p.78 / Chapter 7.3.1 --- Peak ratio of the BE profile --- p.78 / Chapter 7.3.2 --- The initial peak value under the effects of increasing tensile stress --- p.81 / Chapter 7.4 --- Conclusions --- p.82 / Figures for chapter7 --- p.83 / Chapter 8 --- Experiments and Results: The Recovery of Strained Steel Bars by Annealing --- p.94 / Chapter 8.1 --- Introduction --- p.94 / Chapter 8.2 --- Experiments --- p.94 / Chapter 8.2.1 --- Measurement of annealed sample (Set D) --- p.95 / Chapter 8.2.2 --- Results of the Set E samples --- p.95 / Chapter 8.3 --- Results and discussions --- p.95 / Chapter 8.3.1 --- Hardness --- p.96 / Chapter 8.3.2 --- Peak ratio of the BE profile --- p.97 / Chapter 8.3.3 --- BE profile for the samples of Set E --- p.98 / Chapter 8.4 --- Conclusions --- p.99 / Figures for chapter8 --- p.100 / Chapter 9 --- Conclusions and Suggestions for Further Studies --- p.104 / Bibliography --- p.108

La superélasticité (SE) est la capacité d'un alliage à recouvrer sa forme initiale après une importante déformation. Cet effet, dû à une transformation martensitique réversible, est très convoité pour de nombreuses applications biomédicales. Les alliages nickel-titane sont les alliages les plus utilisés dans les applications fonctionnelles nécessitant de la SE. Cependant, l'utilisation de cet alliage dans les dispositifs biomédicaux est controversée par la présence du nickel, considéré comme élément cytotoxique et allergène. De ce fait, ces dernières années, une attention accrue a été portée aux alliages de titane [3-métastable pouvant constituer une alternative pour des applications biomédicales. En effet, ils ont l'avantage d'être élaborés à partir d'éléments biocompatibles et de présenter un comportement SE. L'objectif de cette thèse réside ainsi dans l'étude de la réponse SE des alliages de titane [3-métastable à différentes échelles dans leur forme massive et sous forme de revêtements. Deux alliages [3-métastable ont été élaborés: le Ti-27Nb {% at) et le Ti-24Nb-4Zr-4Sn (% mass). Les propriétés SE de ces alliages à l'état massif ont été caractérisées à l'échelle macroscopique et à l'échelle submicrométrique et comparées à celles du NiTi superélastique et du CP-Ti élasto-plastique. La nanoindentation a d'abord été utilisée pour sonder l'effet SE dans ces alliages massifs à l'échelle locale, et dans un deuxième temps, pour étudier l'effet de l'orientation cristallographique sur la réponse SE et mécanique à l'échelle du grain. Enfin, les propriétés mécaniques et SE de ces alliages sous forme de revêtements ont été évaluées avec ce même procédé de nanoindentation. / The superelasticity is the ability of an alloy to recover its original shape after significant deformation. This effect, due to a reversible stress-induced martensitic transformation, is highly sought after for many biomedical applications. Nickel-titanium alloys that have a very large strain recovery (in bulk and thin film state), are the alloys currently used for functional applications requiring superelasticity. However, the use of this alloy in biomedical devices is controversial by the presence of nickel, considered as allergen and presumed cytotoxic for the body. As a result, in recent years, increased attention has been given to metastable f3 titanium alloys, which may be an alternative for biomedical applications. Indeed, they have the advantage of being elaborated from biocompatible elements and exhibit a superelastic behavior. The objective of this thesis lies in the study of the superelastic response of metastable f3 titanium alloys at different scales in bulk and thin film state. Two metastable f3 titanium alloys were elaborated: Ti-27Nb (at%) alloy and Ti-24Nb-4Zr-8Sn (wt %) alloy. The superelastic properties of these two bulk alloys were characterized at macroscopic and sub-micrometric scale and compared to superelastic NiTi and elastoplastic CP-Ti. The nanoindentation was first used to evaluate the superelastic effect of various bulk titanium alloys at local scale, and in a second time, to study the effect of crystallographic orientations on the superelastic and mechanical responses at the grain scale. Finally, the mechanical and superelastic properties of metastable f3 titanium coatings were evaluated with this same nanoindentation process.