[EN] Ti and its alloys are mostly used biomaterials due to its unique properties like (high corrosion resistance, low elastic modulus, high mechanical strength/ density and good biocompatibility). Ti β alloys based on the Ti-Mo alloy system shows unique properties to employ as biomaterials. Tiβ alloys have lower Young Modulus, shielding stress and lower bone reabsorption. This research aims to develop a new biomaterial for a dental implant. This research evaluates the addition of Zr and a small amount of Fe on the β-phase stability and the mechanical properties of Ti-Mo alloy to be employed for the medical applications. These alloys had been produced using two powder metallurgy (PM) techniques; first technique is elemental blending (EB) which had been selected because it enhanced the surface contact between the alloying element and Titanium (Ti) with a cost-effective route. The behavior of different Ti alloys composition was evaluated using this technique. Samples were uniaxial pressed at 600 MPa and sintered at 1250ºC. Second technique evaluated in this study was Mechanical alloying (MA). This technique has higher mixing energy than elemental blend which improves mechanical contact between different particles, and it helps diffusion during the sintering process. Samples were pressed at 600 MPa initially, and after evaluating mechanical properties, compaction pressure is changed to 900 MPa for a high green density of powders. Different mechanical tests and microstructural studies were performed for elemental blend (EB) samples and for mechanical alloying samples to ensure the properties suitable for biomedical applications. Different tests for MA are Fluidity test (suitable to know about the flow of the powder after milling cycle) and Granulometric Analysis (test is suitable for powder distribution analysis). Other tests are common like Archimedes test which is suitable for calculating the porosity of the sintered samples, Three-point bending test is suitable for knowing Bending strength of the sintered samples and to know energy conserved by the breaking samples, Ultrasonic test performed for knowing elastic modulus of the alloys, Hardness test performed for calculating the Vicker´s hardness of the alloy, SEM analysis performed to know about microstructure and EDX analysis(by which proper mixing of the alloying element with the central element would be known). EBSD (Electron Beam Scattered Diffraction) is also performed for more analysis about microstructure, grain size, mixing of different elements in alloys. EBSD is an excellent tool for microanalysis of the material. From the results section, Green density of the alloy, fluidity of the milled powder, Granulometry of the powder, sintered density of the alloy (From Archimedes test), bending strength and bending modulus of the alloy, Elastic modulus by Ultrasonic test, Microstructure of the alloy(By SEM and EBSD Analysis of the sintered part.) are determined. Green density for elemental blend alloys is in the range of (77.42- 78.11%) and for Mechanical alloying samples were (74.94-78.58%). Sintered density obtained by Archimedes' test for the elemental blend is in the range of (96.88- 98.74%). Bending strength obtained from three-point bending test is in range of (666-2161 MPa), and mechanical alloying is in range of (371-1597 MPa). From the high test, Determined Elastic modulus of the alloy is in range of (95.5-103 GPa) and for Mechanical Alloying elastic modulus was in the range of (66-82 GPa), which would be more suitable for biomedical applications. (From the SEM and EBSD analysis Mechanical alloying are more homogeneous mixing in comparison to Elemental Blend. Green density (just after compaction) for the elemental blend is more than mechanical alloying so that Sintered Density for Elemental Blend is more than Mechanical Alloying. Due to higher sintered density, porosity is more in case of the elemental blend. Also, due to higher porosity, bending strength is low in case of mechanical alloying with same sintering parameters as Elemental blend alloys. Micro-Hardness value is more in case of elemental blend in comparison to Mechanical Alloying. Elastic modulus is more in case of elemental blend in comparison to mechanical alloying; lower elastic modulus is more suitable for biomedical applications. Grains are more regular and smaller in case of Mechanical alloying which is due to a more homogeneous distribution of the elements in comparison to elemental blend. Powder processing technique is changed from Elemental Blend to Mechanical Alloying due to the improvement of homogeneity of green powders. Mechanical Alloying produced more homogeneous mixture due to high-speed milling with higher Ball to powder ratio (which generates higher energy within the jars and breaks the powders into smaller particles). Different combination of milling speed and milling time performed for our results and the effects of a combination of different parameters observed. / [ES] El titanio y sus aleaciones son los biomateriales principalmente usados debido a sus propiedades únicas como alta resistencia a la corrosión, bajo módulo de elasticidad, alta resistencia mecánica/densidad y buena biocompatibilidad. Las aleaciones Tiβ basadas en el sistema de aleación Ti-Mo muestran propiedades únicas para emplearse como biomateriales. Las aleaciones de Tiβ tienen un módulo de Young más bajo, menor apantallamiento de tensiones y menor reabsorción ósea. Esta investigación tiene como objetivo desarrollar un nuevo material biológico para un implante dental. Esta investigación evalúa la adición de Zr y una pequeña cantidad de Fe sobre la estabilidad de fase β y las propiedades mecánicas de la aleación de Ti-Mo que se utilizará para las aplicaciones médicas. Estas aleaciones se han producido utilizando dos técnicas de pulvimetalurgia (PM); La primera técnica es la combinación de polvos elementales (EB) que se ha seleccionado porque mejora el contacto superficial entre el elemento de aleación y el titanio (Ti) con una ruta rentable. El comportamiento de diferentes composiciones de aleaciones de Ti se evaluó utilizando esta técnica. Las muestras se prensaron uniaxialmente a 600 MPa y se sinterizaron a 1250ºC. La segunda técnica evaluada en este estudio fue la aleación mecánica (MA). Esta técnica tiene una mayor energía de mezcla que la mezcla elemental, lo que mejora el contacto mecánico entre las diferentes partículas y ayuda a la difusión durante el proceso de sinterización. Las muestras se prensaron, igualmente, a 600 MPa inicialmente, y después de evaluar las propiedades mecánicas, la presión de compactación se aumentó a 900 MPa para una mayor densidad en verde de los polvos. Se realizaron diferentes pruebas mecánicas y estudios microestructurales para las muestras de mezcla elemental (EB) y las muestras de aleación mecánica (MA) para garantizar las propiedades adecuadas para aplicaciones biomédicas. Las diferentes pruebas para MA han sido la fluidez, adecuada para conocer el flujo del polvo después del ciclo de molienda, y el análisis granulométrico, adecuado para el análisis de la distribución del tamaño de los polvos. Otras pruebas comunes como la determinación de la densidad por el método de Arquímedes, adecuada para calcular la porosidad de las muestras sinterizadas, el ensayo de flexión a tres puntos para conocer las propiedades mecánicas de las muestras sinterizadas y conocer la energía conservada por las muestras a rotura, y la dureza Vickers de las aleaciones. Mediante ultrasonidos se ha determinado el módulo elástico de las aleaciones. El análisis microestructural se ha realizado mediante microscopía electrónica de barrido y análisis por energías dispersivas de rayos X mediante los que se ha determinado la homogeneidad química de las aleaciones. La difracción de electrones retrodispersados (EBSD) ha permitido obtener la orientación cristalina de cada grano y su tamaño, pues resulta una excelente herramienta para el microanálisis del material. La densidad en verde para aleaciones de mezcla elemental está en el rango del 77.42- 78.11% y para las muestras de aleación mecánica se han obtenido densidades relativas del 74.94-78.58%. La densidad de los sinterizados, obtenida por el método de Arquímedes, está en el rango del 96.88-98.74%, para la mezcla elemental de polvos. La resistencia a la flexión obtenida a partir de la prueba de flexión a tres puntos está en un amplio rango de 666 a 2161 GPa, mientras que para los polvos de aleación mecánica se encuentra en el rango de los 371 a 1597 GPa. El módulo elástico determinado en las aleaciones obtenidas con polvos de mezcla elemental está en el rango de los 95.5 a los 103 GPa, mientras que, en las obtenidas con los polvos mezclados mecánicamente, su módulo elástico oscila entre los 66 y los 82 GPa, que sería más adecuado para un menor apantallamiento de tensiones. La microestructura de las muestras procesadas con polvos elementales con polvos mezclados mecánicamente, presentan diferencias sustanciales con un afinamiento del tamaño de grano con los polvos mezclados mecánicamente, aunque aparecen claramente diferenciadas dos fases distintas y una mayor proporción de fase . Debido a la menor densidad de las muestras procesadas con los polvos mezclados mecánicamente, estas presentan una menor resistencia mecánica y a su vez una menor plasticidad. Por ello se opta por utilizar técnicas de sinterización de alta densificación como el Spark Plasma Sinterirng (SPS) a pesar de lo cual no obtenemos mejora en el comportamiento mecánico de las mismas. Sin embargo, en los ensayos de corrosión y liberación de iones si se ha encontrado una sustancial mejor en las muestras obtenidas por SPS. / [CA] El titani i els seus aliatges són utilitzats, principalment, com a biomaterials per les seves propietats úniques com alta resistència a la corrosió, baix mòdul d'elasticitat, alta resistència mecànica específica i bona biocompatibilitat. Els aliatges β Ti basades en el sistema d'aliatge Ti-Mo mostren propietats úniques per a emprar-se com biomaterials. Els aliatges de β Ti tenen un mòdul de Young més baix, menor apantallament de tensions i menor reabsorció òssia. Aquesta investigació té com a objectiu desenvolupar un nou material biocompatible per a la seva aplicació com a implants dentals. Aquesta investigació avalua l'addició de Zr i petites quantitats de Fe sobre l'estabilitat de la fase β i les propietats mecàniques dels aliatges Ti-Mo que s'utilitzaran per a aplicacions biomèdiques. Aquests aliatges s'han produït utilitzant dues tècniques pulvimetalúrgiques (PM); La primera tècnica és la mescla elemental de pols (EB) que s'ha seleccionat perquè millora el contacte superficial entre l'element d'aliatge i el titani (Ti) amb una ruta rendible. El comportament de diferents composicions d'aliatges de Ti s'ha avaluat utilitzant aquesta tècnica. Les mostres es van premsar uniaxialment a 600 MPa i es sinteritzaren a 1250ºC. La segona tècnica avaluada en aquest estudi va ser l'aliatge mecànica (MA). Aquesta tècnica té una major energia de mescla que la mescla elemental, el que millora el contacte mecànic entre les diferents partícules i ajuda a la difusió durant el procés de sinterització. Les mostres es van premsar a 600 MPa inicialment, i després d'avaluar les propietats mecàniques, la pressió de compactació es va augmentar a 900 MPa per a una major densitat en verd de les pols. Es van realitzar diferents proves mecàniques i estudis microestructurals per a mostres de mescla elemental (EB) i per a mostres d'aliatge mecànica per garantir les propietats adequades per a aplicacions biomèdiques. Les diferents proves per MA són la prova de fluïdesa (adequada per conèixer el flux de la pols després del cicle d'aliatge mecànica) i l'anàlisi granulomètric (la prova és adequada per a l'anàlisi de distribució de la mida de les pols). S'han realitzat altres proves comunes com la prova d'Arquímedes, adequada per a calcular la porositat de les mostres sinteritzades. La prova de flexió de tres punts és adequada per conèixer la resistència a la flexió de les mostres sinteritzades i conèixer l'energia conservada per les mostres durant el seu trencament. Mitjançant ultrasons s'ha determinat el mòdul elàstic dels aliatges i la duresa s'ha realitzat per calcular la duresa Vickers de l'aliatge. S'ha realitzat l'anàlisi per SEM per conèixer la microestructura i l'anàlisi per EDX (mitjançant el qual es coneixeria la mescla adequada de l'element d'aliatge amb l'element central). EBSD (difracció d'electrons retro dispersats) també es realitza per a un més complet anàlisi sobre la microestructura, orientacions cristal·lines, mida de gra, mescla de diferents elements en els aliatges. EBSD és una excel·lent eina per al microanàlisi del material. De la secció de resultats es determinen la densitat en verd de l'aliatge, fluïdesa de la pols mòlta, granulometria de la pols, densitat de l'aliatge sinteritzada (prova d'Arquímedes), resistència a la flexió i mòdul a flexió de l'aliatge, mòdul elàstic per ultrasons, microestructura de l'aliatge (per SEM i EBSD). La densitat en verd per als aliatges de mescla elemental està en el rang dels 77.42-78.11%, mentre que per a les mostres d'aliatge mecànica van ser d'un 74.94-78.58%. La densitat dels sinteritzats, obtinguda pel mètode d'Arquímedes, està en el rang dels 96.88-98.74%, per la mescla elemental de pols. La resistència a la flexió obtinguda a partir de la prova de flexió de tres punts es troba en el rang dels 666-2161 MPa, mentre que per a les mostres de aliat mecànic el seu rang és molt ampli, des dels 371 als 1597 MPa. A partir de l'assaig d'ultrasons, el mòdul elàstic determinat per als aliatges de mescla elemental està en el rang de 95.5 a 103 GPa i per a les sinteritzades amb pols aliats mecànicament, es troba en el rang dels 66-82 GPa, que seria més adequat per a aplicacions biomèdiques. A partir de les anàlisis per SEM i EBSD, es confirma que l'aliatge mecànica és una mescla més homogènia en comparació amb la mescla elemental dels pols. La densitat en verd (just després de la compactació) per a la mescla elemental és més gran que en l'aliatge mecànica, de manera que la densitat sinteritzada per a la mescla elemental és major igualment que en l'aliatge mecànica. A causa d'una major densitat dels sinteritzats, la porositat és menor en el cas de la mescla elemental. A més, a causa d'una major porositat, la resistència a la flexió és baixa en cas d'aliatge mecànica amb els mateixos paràmetres de sinterització que els aliatges de mescla elemental. El valor de microduresa és major en el cas de la mescla elemental en comparació amb l'aliatge mecànica. El mòdul elàstic també resulta més gran en el cas d'una mescla elemental comparat amb l'aliatge mecànica, que en aquest cas resultaria més adequat per a aplicacions biomèdiques. Els grans són més regulars i més petits en el cas de l'aliatge mecànica, a causa d'una distribució més homogènia dels elements en comparació amb la mescla elemental i als efectes de recristal·lització durant la sinterització. L'aliatge mecànica va produir una mescla més homogènia dels elements d'aliatge, a causa de la mòlta a alta velocitat amb una relació boles/pols més alta que genera una major energia dins de les gerres i obté partícules de pols més petites. S'ha realitzat una combinació de diferents velocitats i temps de mòlta, optimitzant aquests paràmetres per a les nostres aliatges. / Mohan, P. (2020). Development of new high performance Titanium alloys with Fe-addition for dental implants [Tesis doctoral no publicada]. Universitat Politècnica de València. https://doi.org/10.4995/Thesis/10251/147859 / TESIS

Master´s thesis is focus on the proces of mechanical alloying. It is the proces of modifying a hetegeneous mixture of powder materials into a homogeneous composite powder. Experiments are focus on three types of composite materials. A magnetic soft alloy Permalloy, ODS steel based on commercially available powder steel 434 LHC and low-activation high-chrome ODS steel 14Cr-2W. On composite powders are made a series of mechanical tests and chemicel analysis. Based on this tests and analysis it was possible to confirm the milling time needed to create fully homogeneous composite powder. Next step is compaction of composite powder into compact volume and another mechanical tests ana analysis of microstructure. In these analyzes to determine whether i tis necessary to use protective atmosphere during mechanical alloying. All three type of materials succesfull prepared by mechanical alloying. It was found that for created of a fully homogeneous composite powder is necessary to perform mechanical alloying for 24 hours. When processing of corrosion resistant materials, i tis possible to perform mechanical alloying in an air atmosphere. During mechanical alloying materials which are subject to oxidation, i tis necessary to use protective atmosphere.

京都大学 / 0048 / 新制・課程博士 / 博士(エネルギー科学) / 甲第21889号 / エネ博第390号 / 新制||エネ||75(附属図書館) / 京都大学大学院エネルギー科学研究科エネルギー変換科学専攻 / (主査)教授 木村 晃彦, 教授 星出 敏彦, 教授 今谷 勝次 / 学位規則第4条第1項該当 / Doctor of Energy Science / Kyoto University / DGAM

No description available.

A systematic study of iron-based binary and multi-component alloys was undertaken to study the structural evolution in these powders as a function of milling time during mechanical alloying. Blended elemental powders of Fe100-XBX (where x = 5, 10, 17, 20, 22, 25, 37.5 and 50 at. %) and a bulk metallic glass (BMG) composition (Fe60Co8Zr10Mo5W2B15) were subjected to mechanical alloying in a SPEX 8000 mixer mill. X-ray diffraction technique was employed to study the phase evolution, crystallite size, lattice strain and also to determine the crystal structure(s) of the phases. Depending on the milling time, formation of supersaturated solid solutions, intermetallics, and amorphous phases was noted in the binary Fe-B powder mixtures. A maximum of about 22 at. % B was found to dissolve in Fe in the solid state, and formation of FeB and Fe2B intermetallics was noted in some of the powder blends. However, an interesting observation that was made, for the first time, related to the formation of a crystalline phase on continued milling of the amorphous powder in the BMG composition. This phenomenon, termed mechanical crystallization, has been explored. Reasons for the mechanical crystallization of the amorphous powder using the X-ray diffraction and electron microscopy methods have been discussed. External heat treatments of the milled powder were also conducted to study the complete crystallization behavior of the amorphous phase. Preliminary attempts were made to consolidate the milled BMG powder to bulk shape by hot isostatic pressing (HIP) and magnetic compaction techniques. Full densification was not achieved. Nanoindentation and microhardness tests were performed to characterize the mechanical properties of the glassy alloy. Nanoindentation results gave an elastic modulus of 59 GPa, lower than the expected value of 184 GPa; due to the presence of porosity in the consolidated sample. Optimization of the consolidation parameters is required to achieve a fully dense material.

No description available.

Equiatomic composition of Ni and Ti was cryomilled with varying milling times to create Ni-Ti lamella structures with average spacings of 50 nm, 470 nm, and 583 nm in powder particles to vary the interfacial surface area per volume. These surfaces form interfaces for diffusion that are essential for solid state amorphization during low temperature annealing. To compare solid state amorphization in a relatively defect free multilayer system, elemental Ni and Ti were deposited by electron beam physical vapor deposition on titanium plates with comparable spacing as above. Both milled and deposited multilayers were annealed between 225 and 350°C for up to 50 hours. X-ray diffraction characterization and in situ annealing was conducted on cryomilled and deposited multilayers of Ni-Ti. Based on this characterization, an amorphization model based on the Johnson-Mehl-Avrami nucleation and growth equation has been established to predict the amorphization of both cryomilled and deposited multilayers. Cryomilled powders experienced much larger amorphization rates during annealing than that of deposited multilayer structures, for all layer spacings. This superior amorphization is seen despite the formation of amorphous phase during the milling process; the amount of which increases with increasing milling time. The difference in amorphization rates between cryomilled and deposited multilayers is attributed to excess driving force due to the extensive preexisting defects in the powders caused by cryomilling. Serial 3D reconstruction of cryomilled Ni-Ti powders was done by scanning electron microscopy and focused ion beam. Through 3D reconstruction it was observed that a random and non-linear lamella structure has been formed in cryomilled powders. Furthermore, lamellar spacing was seen to become smaller with increased milling time while at the same time becoming more homogeneous through the material's volume. 3D reconstruction of cryomilled Ni-Ti offers a unique insight into the microstructures and surface areas of cryomilled powder particles that has never been accomplished. / Ph. D.

Magnetic alloys that are amorphous exhibit soft magnetic properties; hence they play an essential role in electronic and electrical systems and devices. They are used in applications that include electrical power generation and transmission, electronic motors, solenoids, relays, magnetic shielding, and electromagnets. This work was an attempt to investigate the solid-state formation of Co-C amorphous alloys, their thermal stability and magnetic properties. Amorphous Co-C alloys with compositions of 2 to 40 at.% C were successfully synthesized from elemental Co and C (graphite) using mechanical alloying, a solid-state powder processing technique. All alloy compositions were milled for up 40 hours. After 20h of milling some of the alloys (≤ 20 at.% C) had partially amorphized, while the higher concentrations had completely amorphized. After 40h of milling, complete amorphization was observed in all alloys, except for the 2 and 5 at.% C alloys. The thermal analyses of the milled powders showed very interesting results. DSC results indicated that alloys with compositions through 20 at.% C crystalized in two steps; the lower temperature event precipitated metastable cobalt carbide from the amorphous phase, followed by the eventual transformation to fcc cobalt and graphite from both the remaining amorphous and the metastable carbide at the higher temperature. Two types of carbides were observed - Co3C in the 2 and 5 at.% C alloys, and Co2C in the higher carbon alloys through 20 at.% C. For compositions above 20 at.% C, only one step crystallization was observed, that of the decomposition of the amorphous phase to amorphous carbon and cobalt – primarily fcc phase. Activation energy calculations show that the low temperature carbide precipitation was controlled by carbon diffusion, while the high temperature decomposition reaction forming cobalt and amorphous carbon was controlled by cobalt diffusion. Room temperature magnetic measurements of the milled powders were made using vibrating sample magnetometer (VSM). High saturation magnetization (Ms) and very low coercivity (Hc) are desired for efficient performance of soft magnets. But in this study, Ms decreased with both carbon composition and milling time. It decreased from 195 Am2/kg for the un-milled pure Co to between 178 and 44 Am2/kg for the alloys, with the worst being the 40 at.% C sample milled for 40h. The Ms drop as function of composition made sense, as its related to the volume fraction of cobalt in the alloy. However, the Ms drop as a function of milling time is unclear. In the case of Hc, its value did drop from 12.7 kA/m for the un-milled pure Co to between 7.5 and 1.3 kA/m when the C content is less than 15 at.%. These gains are not significant enough to favor the use of these alloys as soft magnets. Amorphous metal alloys tend to have strengths that are much higher than their crystalline counterparts, and they have hardness values comparable to those of particulate ceramic materials used to reinforce metal matrices. The Co-C amorphous alloy with 40 at.% C that had been milled for 40h (the most stable of all the samples) was used to reinforce cobalt matrix by powder processing methods that included spark plasma sintering (SPS) at temperatures below those of crystallization. Volume fraction ranged from 1 to 20 % reinforcement. The densities of these composites were between 81 and 85 % of theoretical values, hence there were substantial porosities. Despite this the matrix strengthening of the cobalt matrix, as assessed by Vickers microhardness tests, was significant. Hardness increased from 210 HV for unreinforced matrix to 537 HV for the 20 vol.% amorphous. The primary contributor to the strengthening appears to be boundary strengthening by the particles whose average size of about 4 microns is comparable to the grain size of the matrices of the composites. The hardness data fits the Hall Petch-like relationship based on particle spacing. Having a reinforcement particle with a chemistry similar to that of the matrix as is the case in this study, has the potential to improve interfacial bonding and also minimize the difference between the components' coefficient of thermal expansions, which are major issues with the use of ceramics to reinforce metal matrices. The microstructures of the composites indicated good bonding at their interfaces. / Doctor of Philosophy / Magnetic alloys that are amorphous (have no long-range atomic order) exhibit soft magnetic material properties (easily magnetized and demagnetized); hence they play an essential role in electronic and electrical applications. This work investigated the solid-state formation of Cobalt-Carbon (Co-C) amorphous alloys, their thermal stability and magnetic properties. Amorphous Co-C alloys with compositions of 2 to 40 atomic weight % of C were successfully synthesized from elemental Co and C (as graphite) using a mechanical alloying technique (high-energy milling to alloy materials by impact). All alloy compositions were milled for up 40 hours. After 20h of milling some of the alloys (≤ 20 atomic weight % of C) had partially become amorphous, while the higher concentrations had completely become amorphous. After 40h of milling, complete amorphization was observed in all alloy compositions, except for the 2 and 5 atomic weight % of C alloys (2-5 atomic weight % of C). Thermal analyses (Differential Scanning Calorimetry, DSC) of the milled powders showed that alloys with compositions through 20 atomic weight % of C crystalized via a low temperature precipitation of a metastable cobalt carbide from the amorphous phase, followed by a high temperature transformation to a face centered cubic (fcc) cobalt and graphite phase from both the remaining amorphous and the metastable carbide. Activation energy calculations showed that the low temperature carbide precipitation was controlled by carbon diffusion, while the high temperature decomposition reaction forming cobalt and amorphous carbon was controlled by cobalt diffusion. High saturation magnetization (Ms) and very low coercivity (Hc) are desired for efficient performance of soft magnets. Thus, room temperature magnetic measurements of the milled powders were made using vibrating sample magnetometer (VSM). But in this study, Ms decreased with both carbon composition and milling time. The Ms drop as function of composition made sense, as its related to the volume fraction of cobalt in the alloy. However, the Ms drop as a function of milling time is unclear. In the case of Hc, its value did drop from 12.7 kA/m for the un-milled pure Co to between 7.5 and 1.3 kA/m when the C content is less than 15 atomic weight %. These gains are not significant enough to favor the use of these alloys as soft magnets. Amorphous metal alloys tend to have strengths that are much higher than their crystalline counterparts, and they have hardness values comparable to those of particulate ceramic materials used to reinforce metal matrices. The Co-C amorphous alloy with 40 atomic weight % of C that had been milled for 40h was used to reinforce cobalt matrix by powder processing methods (including spark plasma sintering (SPS) at temperatures below those of crystallization). The densities of these composites were between 81 and 85 % of theoretical values and hence there was substantial porosity. Despite this the matrix strengthening of the cobalt matrix, as assessed by Vickers microhardness tests, was significant. The primary contributor to the strengthening appeared to be boundary strengthening by the particles whose average size of about 4 microns was comparable to the grain size of the matrices of the composites. Having a reinforcement particle with a chemistry similar to that of the matrix has the potential to improve interfacial bonding and also minimize the difference between the components' coefficient of thermal expansions, which are major issues with the use of ceramics to reinforce metal matrices. The microstructures of the composites indicated good bonding at their interfaces.

No description available.

Made available in DSpace on 2017-07-21T20:42:38Z (GMT). No. of bitstreams: 1 JOEVERTON IURP PEREIRA.pdf: 10346836 bytes, checksum: 7a9cb51468fd6451b35517266553a7b7 (MD5) Previous issue date: 2012-09-19 / Coordenação de Aperfeiçoamento de Pessoal de Nível Superior / The alloys of Ni-Cr-Al-C system were synthesized by mechanical alloying, as a proposal of an alternative processing route, in order to improve the microstructure control regarding to a more homogeneous distribution of both Ni3Al precipitates and dispersed chromium carbides, characteristics phases of NiCrAlC alloys. It were chosen 15 compositions, comprised within a range present in the literature, with carbon content variations between 0,5 to 1,5%wt, chromium between 7,5 to 11%wt, and aluminum in the same way as chromium. The milling products were compressed and sintered at 1200°C for a period of 2 hours, and the results of the analysis by Xray diffraction, optical microscopy, scaning electron microscopy (SEM), energy dispersion analysis (EDS) and hardness were compared with some foundry products presents in the literature. The NiCrAlC alloys studied at this work presented nanometric Ni3Al ( phase) precipitates, which provided a hardness that is comparable to that of alloys made by casting followed by heat treating, in spite of exhibit a significant porosity. At the same way, the chromium carbides showed finely dispersed in the matrix, and homogeneously distributed. / Ligas do sistema Ni-Cr-Al-C foram sintetizadas por moagem de alta energia, como proposta de uma rota alternativa de processamento, visando um melhor controle da microestrutura no que concerne a uma distribuição mais homogênea tanto dos precipitados de Ni3Al quanto dos carbetos de cromo dispersos, fases características das ligas NiCrAlC. Foram escolhidas 15 composições compreendidas dentro de uma faixa presente na literatura, com variações de carbono entre 0,5 e,1,5%, de cromo entre 7,5 e 11%, e alumínio da mesma forma que o cromo. Os produtos de moagem foram compactados e sinterizados à 1200°C por um período de 2h, e os resultados das análises de difração de raios x, microscopia ótica e eletrônica, análise por dispersão de raios x e dureza realizadas foram comparados com algumas ligas fundidas presentes na literatura. As ligas NiCrAlC estudadas apresentaram precipitados nanométricos de Ni3Al (fase ), que proporcionaram uma dureza comparável à das ligas produzidas por fusão seguidas de tratamento térmico, apesar de exibirem uma porosidade significativa. Do mesmo modo os carbetos de cromo mostraram-se finamente dispersos na matriz, e homogeneamente distribuídos.