Relevant bibliographies by topics / Diffusional Creep

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  1. Journal articles
  2. Dissertations / Theses
  3. Books
  4. Book chapters
  5. Conference papers
  6. Reports

Academic literature on the topic 'Diffusional Creep'

Author: Grafiati
Published: 4 June 2021
Last updated: 7 September 2023

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Journal articles on the topic "Diffusional Creep"

1

Greenwood, G. W. "Diffusional Creep." Defect and Diffusion Forum 66-69 (January 1991): 1187–204. http://dx.doi.org/10.4028/www.scientific.net/ddf.66-69.1187.

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2

Mesarovic, Sinisa Dj. "Lattice continuum and diffusional creep." Proceedings of the Royal Society A: Mathematical, Physical and Engineering Sciences 472, no. 2188 (2016): 20160039. http://dx.doi.org/10.1098/rspa.2016.0039.

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Diffusional creep is characterized by growth/disappearance of lattice planes at the crystal boundaries that serve as sources/sinks of vacancies, and by diffusion of vacancies. The lattice continuum theory developed here represents a natural and intuitive framework for the analysis of diffusion in crystals and lattice growth/loss at the boundaries. The formulation includes the definition of the Lagrangian reference configuration for the newly created lattice, the transport theorem and the definition of the creep rate tensor for a polycrystal as a piecewise uniform, discontinuous field. The values associated with each crystalline grain are related to the normal diffusional flux at grain boundaries. The governing equations for Nabarro–Herring creep are derived with coupled diffusion and elasticity with compositional eigenstrain. Both, bulk diffusional dissipation and boundary dissipation accompanying vacancy nucleation and absorption, are considered, but the latter is found to be negligible. For periodic arrangements of grains, diffusion formally decouples from elasticity but at the cost of a complicated boundary condition. The equilibrium of deviatorically stressed polycrystals is impossible without inclusion of interface energies. The secondary creep rate estimates correspond to the standard Nabarro–Herring model, and the volumetric creep is small. The initial (primary) creep rate is estimated to be much larger than the secondary creep rate.
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Wolfenstine, J., T. R. Armstrong, W. J. Weber, M. A. Boling-Risser, K. C. Goretta, and J. L. Routbort. "Elevated temperature deformation of fine-grained La0.9Sr0.1MnO3." Journal of Materials Research 11, no. 3 (1996): 657–62. http://dx.doi.org/10.1557/jmr.1996.0079.

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Compressive creep behavior of fine-grained (5 μm) La0.9Sr0.1MnO3with a relative theoretical density between 85 and 90% was investigated over the temperature range 1150–1300 °C in air. The fine grain size, brief creep transients, stress exponent close to unity, and absence of deformation-induced dislocations, suggested that the deformation was controlled by a diffusional creep mechanism. The activation energy for creep of La0.9Sr0.1MnO3was 490 kJ/mole. A comparison of the activation energy for creep of La0.9Sr0.1MnO3with existing diffusion and creep data for perovskite oxides suggested that the diffusional creep of La0.9Sr0.1MnO3was controlled by lattice diffusion of the cations, either lanthanum or manganese.
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4

Kovacevic, S., and S. Dj Mesarovic. "Diffusion-induced stress concentrations in diffusional creep." International Journal of Solids and Structures 239-240 (March 2022): 111440. http://dx.doi.org/10.1016/j.ijsolstr.2022.111440.

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Berdichevsky, V., P. Hazzledine, and B. Shoykhet. "Micromechanics of diffusional creep." International Journal of Engineering Science 35, no. 10-11 (1997): 1003–32. http://dx.doi.org/10.1016/s0020-7225(97)00005-0.

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Xu, Z. R., and R. B. McLellan. "Hydrogen enhanced diffusional creep." Acta Materialia 46, no. 13 (1998): 4543–47. http://dx.doi.org/10.1016/s1359-6454(98)00152-9.

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Salama, K., G. Majkic, and U. (Balu) Balachandran. "Review: Stress-Induced Diffusion and Cation Defect Chemistry Studies of Perovskites." Defect and Diffusion Forum 242-244 (September 2005): 43–64. http://dx.doi.org/10.4028/www.scientific.net/ddf.242-244.43.

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In this paper we review a number of studies of stress-induced diffusional matter transport in perovskites, with an emphasis on creep studies used as a means of studying defect chemistry on the cation sublattices. Studies of diffusional creep in air or fixed atmospheres are reviewed first, and the common characteristics among these perovskites are identified. Creep studies of several perovskiterelated or perovskite-like structures are reviewed next, and the similarities/dissimilarities to perovskites are outlined. The diffusional creep studies in controlled atmosphere are reviewed next, with the emphasis on defect chemistry modeling from creep data. The paper presents a detailed review of two creep studies in oxygen controlled atmosphere that show particularly interesting and remarkedly different behavior from that predicted by standard defect chemistry models. Defect chemistry modeling from creep data is presented for these two cases. The potential and limitations of using creep experiments for studying diffusional matter transport and cation defect chemistry are discussed.
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8

Jamnik, Janez, and Rishi Raj. "Space-Charge-Controlled Diffusional Creep: Volume Diffusion Case+." Journal of the American Ceramic Society 79, no. 1 (1996): 193–98. http://dx.doi.org/10.1111/j.1151-2916.1996.tb07898.x.

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Greenwood, G. W. "Denuded zones and diffusional creep." Scripta Metallurgica et Materialia 30, no. 12 (1994): 1527–30. http://dx.doi.org/10.1016/0956-716x(94)90302-6.

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Burton, B., and G. L. Reynolds. "In defense of diffusional creep." Materials Science and Engineering: A 191, no. 1-2 (1995): 135–41. http://dx.doi.org/10.1016/0921-5093(94)09643-0.

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Dissertations / Theses on the topic "Diffusional Creep"

1

Westwood, Chris. "Computer simulation of diffusional creep failure of engineering alloys." Thesis, University of Surrey, 2001. http://epubs.surrey.ac.uk/843127/.

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A simplified model with only 2 degrees of freedom is developed for cavity growth along a grain-boundary by surface and grain-boundary diffusion following a similar model for a row of grains used by Sun et al, (1996). A variational principle for the coupled diffusion problem is used to follow the cavity growth. The approximate solution can be reduced to the well-established equilibrium cavity growth model at the fast surface diffusion extreme. By comparing the 2 degree of freedom model with the full finite element solution by Pan et al, (1997), a 'Validity Map' is constructed in terms of the relative diffusivity and applied stress relative to the capillarity stress. It is found that the simplified model accurately describes the evolution process, in terms of overall cavity profile and propagation rate for engineering alloys subject to normal levels of applied stresses. The 2 degree of freedom model for a single cavity was then extended to allow the modelling of multiple cavities. These cavities can be either pre-existing or nucleated during the lifetime of the system. The relative rotation between the grains is also considered. The initial 2 degrees of freedom were increased to six, and a cavity element has been derived. The cavity elements are assembled together using the classical finite element approach. This allows the evolution of multiple cavities and their interactions to be modelled under different applied loads and material parameters. This simplified multiple cavity finite element model was compared with a model for cavity evolution based on a 'smeared-out' approach. It was shown that the 'smeared-out' model does not accurately predict the creep damage for realistic engineering materials and conditions and results in an under prediction of creep lifetime. Using the simplified finite element model the effect of surface diffusion on the evolution of the creep damage was investigated. The evolution of a large pre-existing 'crack-like' cavity was modelled and the effects of nucleation, surface diffusion and loading were also investigated. It was shown that in the majority of cases as the surface diffusion was increased the rupture time was also increased. The results from the large 'crack-like' cavity simulations showed that there was very little crack propagation through the material and the smaller cavities tended to grow independently of the large 'crack-like' cavity.
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Weyer, Royden. "The modelling of damage due to diffusional creep in high chromium steels." Master's thesis, University of Cape Town, 2016. http://hdl.handle.net/11427/22961.

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Understanding the creep deformation of high chromium steels in use in modern power plants has become important in predicting the behaviour and stability of these materials over their operational lifetime. At the deformation rates and conditions recorded in modern power plants, diffusional creep by vacancy migration is seen to be the dominant creep mechanism. However, the understanding of diffusional creep in particle stabilized materials is heavily incomplete. The aim of this project was to model the damage caused by diffusional creep, while considering the microstructure of high chromium steels and the evolution of this microstructure. This problem is addressed by expanding the existing Nabarro-Herring theory on lattice diffusion into a spatially resolved FEM model using MATLAB. This model focussed on adapting the Nabarro-Herring creep model to handle vacancy concentration changes over time. This allowed the model to produce the primary, secondary and tertiary creep stages present in experimental creep tests. As for microstructure, the focus was on adding precipitates (one of the strongest creep strengthening mechanisms) and voids (the largest cause of material damage). During creep exposure, precipitates were subject to coarsening while voids were subject to growth. The primary creep stage was formed by the initial rapid flux of vacancies into the body of the grain, due to large chemical potential gradients. A dynamic equilibrium of vacancy concentration would form within the grain, leading to the secondary creep stage. The creep rate produced was similar to that of the existing theory and it was found to decrease with the introduction of precipitates. This was evaluated by analysing the stress gradients caused by hard particles in a softer matrix. These stress fields lowered the stress in the grain boundaries and thus resulted in fewer vacancies being generated. Coarsening led to a reduction in the stress field distribution and thus resulted in creep strength loss in the material. The inclusion of voids was shown to decrease the initial creep rate, with void growth lessening this effect and leading to the tertiary creep stage. The initial strengthening was due to the void surface replacing the grain boundary as a source of vacancies. As the void surface is a very inefficient source, fewer vacancies were generated, resulting in lower diffusion rates. A slight steady increase in the creep rate over time was shown with the inclusion of void growth. The increase in vacancy generation was caused by the higher stress fields around voids. Initially the stress increase due to a loss in area was accounted for as a stress concentration around the void. Once this void grew too large in relation to the grain size, the stress concentration no longer accounted for all of the stress increase due to load bearing area loss. This resulted in the damage equation coming into play, causing a rapid increase in the stress throughout the grain and leading to the rapid tertiary creep stage.
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Swaroop, N. R. Sathya. "Processing And High Temperature Deformation Of Pure And Magnesia Doped Alumina." Thesis, Indian Institute of Science, 2000. https://etd.iisc.ac.in/handle/2005/180.

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Creep resistance is an important design criterion at high temperatures especially when continuous attempts are made to increase the efficiencies by increasing the operating temperatures. Alumina is an important high temperature material and in addition to that it is used in wide variety of applications such as substrates for electronic packaging, spark plugs, envelopes for sodium vapour lamps, cutting tools (when reinforced with silicon carbide) and in artificial joint prostheses. Studies on creep in alumina. have started as early as 1961. There are differing mechanisms proposed to explain the creep behaviour of alumina in the literature, but until now there is no any unanimous decision as to what the rate controlling mechanism is. Magnesia doped at ppm levels can produce significant changes in the microstructure of alumina, the most important consequence of that being the grain growth inhibition, which renders alumina superplastic. However, in a stoichiometric oxide like alumina, small impurities can create extrinsic defects which would change the diffusivities and creep rates. Therefore the background impurities in alumina should be kept to a minimum, if small dopant effects have to be studied. The present study was undertaken making use of high purity alumina powder and comparing the grain growth and creep properties of pure and magnesia doped alumina, especially since no such investigation was carried out in the recent past with high purity alumina. Pure alumina was processed by cold compaction followed by cold isostatic pressing (CIP) and pressureless sintering in air at 1773 K for 1 hour. Magnesia doped alumina was prepared by calcining a mixture of alumina and magnesium nitrate at 973 K for 2 hours followed by cold compaction, CIPing and pressureless sintering in air at 1773 K. Both pure and magnesia doped alumina were further annealed at 1873 K for various times to get grain sizes in the ranges of 1-5 μm. Grain growth kinetics of pure and magnesia doped alumina were studied at 1823 and 1873 K. The parameter Kg which quantifies the mobility of the grain boundary was got. It was found that Kg had decreased in the magnesia doped alumina (in comparison with pure alumina) by a factor of about 3 to 4 which was marginal and insignificant. The grain sizes followed a log normal distribution in both the cases, indicative of normal grain growth. Creep studies were conducted on pure and magnesia doped alumina in three modes, namely, constant stress, temperature jump and stress jump test. The temperature range used was 1673 to 1773 K and the stress range used was 10 to 100 MPa. The creep parameters were found to be n~1.6, p~3.7 and Q-545 kJ mol"1 for pure alumina and n~l .3, p~3.0 and Q~460 kJ mol-1 for magnesia doped alumina. The creep rates in the case of magnesia doped alumina were found to have increased by a factor of 2 to 3, in comparison with pure alumina. The increase in creep rates were found to be insignificant. The creep data were analyzed and the possibility of the dislocation and interface reaction controlled creep mechanisms were ruled out since they were inconsistent with the data. It was found, from creep parameters and the comparison of theoretical Coble and Nabarro-Herring creep rates with the experimental rates, that Coble creep might be rate controlling. The activation energy values suggested that aluminium ion diffusing along grain boundary might be the rate controlling species. However, when the theoretical creep rates considering various species were compared, the rate controlling species turned out to be oxygen ion diffusing along the grain boundary.
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4

Swaroop, N. R. Sathya. "Processing And High Temperature Deformation Of Pure And Magnesia Doped Alumina." Thesis, Indian Institute of Science, 2000. http://hdl.handle.net/2005/180.

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Creep resistance is an important design criterion at high temperatures especially when continuous attempts are made to increase the efficiencies by increasing the operating temperatures. Alumina is an important high temperature material and in addition to that it is used in wide variety of applications such as substrates for electronic packaging, spark plugs, envelopes for sodium vapour lamps, cutting tools (when reinforced with silicon carbide) and in artificial joint prostheses. Studies on creep in alumina. have started as early as 1961. There are differing mechanisms proposed to explain the creep behaviour of alumina in the literature, but until now there is no any unanimous decision as to what the rate controlling mechanism is. Magnesia doped at ppm levels can produce significant changes in the microstructure of alumina, the most important consequence of that being the grain growth inhibition, which renders alumina superplastic. However, in a stoichiometric oxide like alumina, small impurities can create extrinsic defects which would change the diffusivities and creep rates. Therefore the background impurities in alumina should be kept to a minimum, if small dopant effects have to be studied. The present study was undertaken making use of high purity alumina powder and comparing the grain growth and creep properties of pure and magnesia doped alumina, especially since no such investigation was carried out in the recent past with high purity alumina. Pure alumina was processed by cold compaction followed by cold isostatic pressing (CIP) and pressureless sintering in air at 1773 K for 1 hour. Magnesia doped alumina was prepared by calcining a mixture of alumina and magnesium nitrate at 973 K for 2 hours followed by cold compaction, CIPing and pressureless sintering in air at 1773 K. Both pure and magnesia doped alumina were further annealed at 1873 K for various times to get grain sizes in the ranges of 1-5 μm. Grain growth kinetics of pure and magnesia doped alumina were studied at 1823 and 1873 K. The parameter Kg which quantifies the mobility of the grain boundary was got. It was found that Kg had decreased in the magnesia doped alumina (in comparison with pure alumina) by a factor of about 3 to 4 which was marginal and insignificant. The grain sizes followed a log normal distribution in both the cases, indicative of normal grain growth. Creep studies were conducted on pure and magnesia doped alumina in three modes, namely, constant stress, temperature jump and stress jump test. The temperature range used was 1673 to 1773 K and the stress range used was 10 to 100 MPa. The creep parameters were found to be n~1.6, p~3.7 and Q-545 kJ mol"1 for pure alumina and n~l .3, p~3.0 and Q~460 kJ mol-1 for magnesia doped alumina. The creep rates in the case of magnesia doped alumina were found to have increased by a factor of 2 to 3, in comparison with pure alumina. The increase in creep rates were found to be insignificant. The creep data were analyzed and the possibility of the dislocation and interface reaction controlled creep mechanisms were ruled out since they were inconsistent with the data. It was found, from creep parameters and the comparison of theoretical Coble and Nabarro-Herring creep rates with the experimental rates, that Coble creep might be rate controlling. The activation energy values suggested that aluminium ion diffusing along grain boundary might be the rate controlling species. However, when the theoretical creep rates considering various species were compared, the rate controlling species turned out to be oxygen ion diffusing along the grain boundary.
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Millard, Joseph William. "Pressure Dependence Of The Strength Of Magnesite Deforming By Low Temperature Plasticity, Diffusion Creep, Or Dislocation Creep." University of Akron / OhioLINK, 2018. http://rave.ohiolink.edu/etdc/view?acc_num=akron1526913343559104.

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Mirmasoudi, Sara. "High Temperature Transient Creep Analysis of Metals." Wright State University / OhioLINK, 2015. http://rave.ohiolink.edu/etdc/view?acc_num=wright1452693927.

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McDaniel, Caleb Alan. "The effects of grain size on the strength of magnesite aggregates deforming by low temperature plasticity and diffusion creep." University of Akron / OhioLINK, 2018. http://rave.ohiolink.edu/etdc/view?acc_num=akron1526571269872349.

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Degli, Alessandrini Giulia. "Deformation mechanisms and strain localization in the mafic continental lower crust." Thesis, University of Plymouth, 2018. http://hdl.handle.net/10026.1/12799.

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The rheology and strength of the lower crust play a key role in lithosphere dynamics, influencing the orogenic cycle and how plate tectonics work. Despite their geological importance, the processes that cause weakening of the lower crust and strain localization are still poorly understood. Through microstructural analysis of naturally deformed samples, this PhD aims to investigate how weakening and strain localization occurs in the mafic continental lower crust. Mafic granulites are analysed from two unrelated continental lower crustal shear zones which share comparable mineralogical assemblages and high-grade deformation conditions (T > 700 °C and P > 6 Kbar): the Seiland Igneous Province in northern Norway (case-study 1) and the Finero mafic complex in the Italian Southern Alps (case-study 2). Case-study 1 investigates a metagabbroic dyke embedded in a lower crustal metasedimentary shear zone undergoing partial melting. Shearing of the dyke was accompanied by infiltration of felsic melt from the adjacent partially molten metapelites. Findings of case-study 1 show that weakening of dry and strong mafic rocks can result from melt infiltration from nearby partially molten metasediments. The infiltrated melt triggers melt-rock reactions and nucleation of a fine-grained (< 10 µm average grain size) polyphase matrix. This fine-grained mixture deforms by diffusion creep, causing significant rheological weakening. Case-study 2 investigates a lower crustal shear zone in a compositionally-layered mafic complex made of amphibole-rich and amphibole-poor metagabbros. Findings of case-study 2 show that during prograde metamorphism (T > 800 °C), the presence of amphibole undergoing dehydration melting reactions is key to weakening and strain localization. Dehydration of amphibole generates fine-grained symplectic intergrowths of pyroxene + plagioclase. These reaction products form an interconnected network of fine-grained (< 20 µm average grain size) polyphase material that deforms by diffusion creep, causing strain partitioning and localization in amphibole-rich layers. Those layers without amphibole fail to produce an interconnected network of fine grained material. In this layers, plagioclase deforms by dislocation creep, and pyroxene by microfracturing and neocrystallization. Overall, this PhD research highlights that weakening and strain localization in the mafic lower crust is governed by high-T mineral and chemical reactions that drastically reduce grain size and trigger diffusion creep.
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Aguiniga, Gaona Francisco. "Characterization of design parameters for fiber reinforced polymer composite reinforced concrete systems." Diss., Texas A&M University, 2003. http://hdl.handle.net/1969.1/61.

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Corrosion of steel reinforcement in concrete structures results in significant repair and rehabilitation costs. In the past several years, new fiber reinforced polymer (FRP) reinforcing bars have been introduced as an alternative to steel reinforcing bars. Several national and international organizations have recently developed standards based on preliminary test results. However, limited validation testing has been performed on the recommendations of these standards. High variability of the tensile properties, degradation of tensile strength, direct shear capacity, predicted deflections due to creep, cracking behavior of FRP-reinforced concrete flexural members, bond behavior and development length, and effects of thermal expansion on cracking of FRP reinforced concrete have all been reported, but are areas that need further investigation and validation. The objective of this study is to evaluate the characteristics of glass FRP reinforcing bars and provide recommendations on the design and construction of concrete structures containing these bar types with regard to the areas described. The recently developed ACI 440 design guidelines were analyzed and modifications proposed.
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Rhode, Michael [Verfasser], Thomas [Gutachter] Kannengießer, and Hans [Gutachter] Hoffmeister. "Hydrogen Diffusion and Effect on Degradation in Welded Microstructures of Creep-resistant Low-alloyed Steels / Michael Rhode ; Gutachter: Thomas Kannengießer, Hans Hoffmeister." Berlin : Bundesanstalt für Materialforschung und -prüfung (BAM), 2016. http://d-nb.info/1123074992/34.

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Books on the topic "Diffusional Creep"

1

Cuffin, Sally M. Traveltimes along Clear Creek and selected tributaries upstream from Golden, Colorado, 1996-97. U.S. Dept. of the Interior, U.S. Geological Survey, 1999.

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Cuffin, Sally M. Traveltimes along Clear Creek and selected tributaries upstream from Golden, Colorado, 1996-97. U.S. Dept. of the Interior, U.S. Geological Survey, 1999.

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Cuffin, Sally M. Traveltimes along Clear Creek and selected tributaries upstream from Golden, Colorado, 1996-97. U.S. Dept. of the Interior, U.S. Geological Survey, 1999.

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Williford, Ralph Eric. Matrix creep accommodation in a diffusion controlled phase transformation. 1994.

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Book chapters on the topic "Diffusional Creep"

1

Oberaigner, E. R., and F. D. Fischer. "Diffusional Transformation and Creep in Steels." In Creep in Structures. Springer Berlin Heidelberg, 1991. http://dx.doi.org/10.1007/978-3-642-84455-3_18.

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Gordon, Ronald S. "Diffusional Creep Phenomena in Polycrystalline Oxides." In Point Defects in Minerals. American Geophysical Union, 2013. http://dx.doi.org/10.1029/gm031p0132.

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Spiers, Christopher J., and Peter M. T. M. Schutjens. "Densification of crystalline aggregates by fluid-phase diffusional creep." In Deformation Processes in Minerals, Ceramics and Rocks. Springer Netherlands, 1990. http://dx.doi.org/10.1007/978-94-011-6827-4_13.

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Riedel, Hermann. "Diffusion Creep." In Fracture at High Temperatures. Springer Berlin Heidelberg, 1987. http://dx.doi.org/10.1007/978-3-642-82961-1_26.

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Pelleg, Joshua. "Creep and Its Relation to Diffusion." In Creep in Ceramics. Springer International Publishing, 2017. http://dx.doi.org/10.1007/978-3-319-50826-9_3.

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Henshall, G. A., M. E. Kassner, and R. S. Rosen. "Ambient-Temperature Creep Failure of Silver-Interlayer Diffusion Bonds between Steel." In Diffusion Bonding 2. Springer Netherlands, 1991. http://dx.doi.org/10.1007/978-94-011-3674-7_2.

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Abo-Elsoud, M. "Phenomenological Model for Creep Behaviour in Cu-8.5at%Al Alloy." In Defect and Diffusion Forum. Trans Tech Publications Ltd., 2006. http://dx.doi.org/10.4028/3-908451-28-0.89.

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Bažant, Zdeněk P., and Milan Jirásek. "Temperature Effect on Water Diffusion, Hydration Rate, Creep and Shrinkage." In Creep and Hygrothermal Effects in Concrete Structures. Springer Netherlands, 2018. http://dx.doi.org/10.1007/978-94-024-1138-6_13.

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Kolobov, Yu R., G. P. Grabovetskaya, M. B. Ivanov, R. Z. Valiev, and T. C. Lowe. "Copper Grain Boundary Diffusion and Diffusion Induced Creep in Nanostructured Nickel." In Investigations and Applications of Severe Plastic Deformation. Springer Netherlands, 2000. http://dx.doi.org/10.1007/978-94-011-4062-1_33.

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Vaganov, Danil, and Sergey Zhevnenko. "Determination of Copper Self-Diffusion Coefficients on the Base of High-Temperature Creep Data." In Defect and Diffusion Forum. Trans Tech Publications Ltd., 2006. http://dx.doi.org/10.4028/3-908451-17-5.115.

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Conference papers on the topic "Diffusional Creep"

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Bonora, Nicola, and Luca Esposito. "Mechanism Based Unified Creep Model Incorporating Damage." In ASME 2008 Pressure Vessels and Piping Conference. ASMEDC, 2008. http://dx.doi.org/10.1115/pvp2008-61034.

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Although it is often said that diffusional flow creep is out of the practical engineering applications, the need for a unified model capable to account for the resulting action of both diffusional and dislocation type creep is justified by the increasing demands of reliable creep design for very long lives (exceeding 100.000h), high stress-low temperatures and high temperature-low stress regimes. In this paper, a unified creep model formulation, in which the change of the creep mechanism has been accounted for through an explicit dependence of the exponent n on stress and temperature, has been proposed. The model has been also extended incorporating damage processes, characteristics of creep stage IV, adopting a time independent damage formulation proposed by the authors. An application example of the proposed approach to high purity aluminum is given.
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Dichiaro, Simone, Luca Esposito, and Nicola Bonora. "Evaluation of Constraint Effect on Creep Crack Growth by Advanced Creep Modeling and Damage Mechanics." In ASME 2014 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2014. http://dx.doi.org/10.1115/pvp2014-29105.

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Effects of constraint induced by crack depth and sample geometry on creep crack behavior of high chromium steels was investigated by numerical simulation. An advanced mechanism-based creep model formulation, which accounts for primary and secondary creep stage was used. Here, the transient creep rate is modeled considering the evolution of the internal stress with the activation energy while the steady state creep rate is modelled considering both diffusional and dislocation creep mechanisms. This formulation allows one to predict accurately creep strain accumulation over a wide range of stress and temperature. Model parameters were identified on constant load creep tests and their transferability to the multiaxial state of stress was verified comparing predicted creep life with data obtained on notched bar samples. Continuum damage mechanics was used to predict the occurrence of tertiary creep stage and crack advance. To this purpose, a non-linear damage law, as proposed in Bonora and Esposito [1] was used. The effect of the geometry constrain on creep crack growth was investigated in different sample geometries (C(T), SEN(T), SEN(B), DEN(T) and CCP(T)) for a given crack depth values, and the same biaxiality ratio for SEN(T), SEN(B) and DEN(T). Numerical simulation results were validated by comparison with available experimental data for P91 steels.
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Sharma, Pradeep, and Abhijit Dasgupta. "Micro-Mechanics of Creep-Fatigue Damage in Pb-Sn Solder Due to Thermal Cycling." In ASME 2000 International Mechanical Engineering Congress and Exposition. American Society of Mechanical Engineers, 2000. http://dx.doi.org/10.1115/imece2000-2260.

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Abstract This paper presents a micro-mechanistic approach for modeling fatigue damage initiation due to cyclic creep in eutectic Pb-Sn solder. Damage mechanics due to cyclic creep is modeled with void nucleation, void growth and void coalescence model based on micro-structural stress fields. Micro-structural stress states are estimated under viscoplastic phenomena like grain boundary sliding and its blocking at 2nd phase particles, and diffusional creep relaxation. A conceptual framework is provided to quantify the creep-fatigue damage due to thermo-mechanical cycling. Some parametric studies are provided to better illustrate the utility of the developed model.
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Scano, Lorenzo, and Luca Esposito. "Effects of Primary and Secondary Creep Formulations on API 579-1 Residual Life Evaluation." In ASME 2018 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2018. http://dx.doi.org/10.1115/pvp2018-84407.

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A sound material constitutive equation is crucial for the residual life evaluation of pressure components operating in the creep range. In a previous work [1], the authors investigated how a secondary creep formulation encompassing both the dislocational and the diffusional range influences the assessment of damage according to API 579-1 [2] within the whole component stress range. In the present paper the work has been extended in order to include the effects of primary creep in the constitutive equation for the ASTM A335 P22 low-alloy steel used for the manufacturing of the HRSG header whose welded details were previously investigated. The creep damage was first calculated according to API 579-1 Section 10 via inelastic, time-dependent FEA and the Larson-Miller approach (LMP) with code-defined, minimum time-to-rupture data. This led to a first reckoning of the primary creep impact in terms of API 579-1 residual life for the components under evaluation. The API 579-1 time-to-rupture was then assessed with a detailed stress analysis implementing the Omega Method and its creep strain rate formulation. The obtained results were finally compared to those previously determined through the LMP procedure and the different creep correlations (secondary and primary+secondary).
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Meinshausen, Lutz, Ming Liu, Tae-Kyu Lee, Indranath Dutta, and Li Li. "Reliability Implications of Thermo-Mechanically and Electrically Induced Interfacial Sliding of Through-Silicon Vias in 3D Packages." In ASME 2015 International Technical Conference and Exhibition on Packaging and Integration of Electronic and Photonic Microsystems collocated with the ASME 2015 13th International Conference on Nanochannels, Microchannels, and Minichannels. American Society of Mechanical Engineers, 2015. http://dx.doi.org/10.1115/ipack2015-48124.

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In conjunction with micro bumps, Through-Silicon-Vias (TSVs) are used for die stacking, leading to reduced footprints and a higher performance due to shorter communication bus-length. However the large difference between the thermal expansion of silicon and copper and an increased temperature of the die stack due to Joule heating lead to shear stress at the interface between TSV and substrate. Temperature activated interfacial diffusion in combination with the shear stress leads to diffusional interfacial sliding, resulting in TSV pro- or intrusion. In addition, electromigration (EM) at the interface leads to TSV motion. Against this background the protrusion/intrusion of Cu TSVs (ø 10 μm, length 100 μm) during fast and slow rate thermal cycling (TC) and during EM experiments was investigated. Parallel to the experimental investigation a finite element analysis (FEA) was performed to study the micro-mechanical responses of Cu-filled TSV during thermal cycling. For this purpose interfacial sliding was incorporated into the FE model by diffusional creep mechanism. The FE model captures the main features being observed in experiments such as stress hysteresis and intrusion/protrusion of the TSV relative to Si substrate.
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Li, Xiaolong, Xiao Huang, Qi Yang, and Zhaolin Tang. "Isothermal and Cyclic Oxidation Performance of Vertically Cracked and Columnar TBC Structures Produced Using ASPS Process." In ASME Turbo Expo 2015: Turbine Technical Conference and Exposition. American Society of Mechanical Engineers, 2015. http://dx.doi.org/10.1115/gt2015-42045.

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Oxidation performance of thermal barrier coatings (TBCs) deposited by the axial suspension plasma spraying (ASPS) method was evaluated under isothermal and cyclic conditions with a peak temperature of 1080°C. The TBC systems are based on two nickel-based superalloy substrates (CMSX-4 and IN738LC), platinum aluminide bond coat, and yttria stabilized zirconia (8YSZ) top coat of either vertically cracked (VC) or columnar structure. Samples with IN738LC substrate exhibited longer isothermal oxidation lives whereas the ones with CMSX-4 substrate showed greater cyclic oxidation lives. Outward diffusion of W and Ta in TBC systems containing CMSX-4 was found to have progressed to the interface between TGO and top coat; this has contributed to the reduced isothermal oxidation life. The longer cyclic oxidation lives of TBC systems with CMSX-4 were attributed to less CTE mismatch between coating layers (reduced strain energy) and better creep resistance of diffusional bond coat on CMSX-4, hence less TGO rumpling. TBC systems with columnar YSZ had longer isothermal oxidation lives while those with vertically cracked YSZ seemed to result in longer cyclic lives.
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Gamble, Kyle A. L., Anthony F. Williams, and Paul K. Chan. "A Three-Dimensional Analysis of the Local Stresses and Strains at the Pellet Ridges in a Horizontal Nuclear Fuel Element." In 2014 22nd International Conference on Nuclear Engineering. American Society of Mechanical Engineers, 2014. http://dx.doi.org/10.1115/icone22-30023.

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A three-dimensional finite element model is being developed for a quarter fuel element, which is equivalent to a full fuel element using symmetry. The model uses the Multiphysics Object-Oriented Simulation Environment (MOOSE) framework developed at Idaho National Laboratory. The model facilitates an in-depth investigation into a variety of deformation phenomena for a horizontal nuclear fuel element including bowing, sagging, and stresses and strains. This paper presents a preliminary analysis of the local stresses and strains of the sheath (clad) at the pellet-to-pellet interfaces for low, normal and high linear powers. During irradiation the fuel pellets thermally expand and take on an hourglass shape. The hourglassing behaviour leads to higher local stresses and strains in the sheath at the locations of the pellet-to-pellet interfaces. The purpose of this work is to quantify these stresses and strains for varying linear powers, and to illustrate the effect that the material model chosen for the cladding has on the results. Preliminary results are presented for two sheath types: elastic, and elastic including diffusional creep. These models are benchmarked against a validated industry code called ELESTRES. The results indicate that the predicted sheath hoop strain is about half of what is determined by ELESTRES in both the elastic and elastic-creep cases. This highlights the requirement of a pellet cracking model in three-dimensional simulations. The elastic-creep model predicts less stress within the sheath than the elastic model as expected.
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Liu, Yi, Kelly Shue, Xin Wu, Zhicheng Li, and Yongbo Xu. "Superplasticity and Microstructural Evolution of a Large-Grained Mg Alloy." In ASME 2000 International Mechanical Engineering Congress and Exposition. American Society of Mechanical Engineers, 2000. http://dx.doi.org/10.1115/imece2000-1818.

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Abstract Commercial Mg-3Al-Zn alloys (AZ31) with initial large grains (∼250μm) has been found superplastic at a strain rate of 0.5×10−2s−1 and at 350–500 C. The maximum elongation to failure of 170% at 500°C was obtained. Scanning electron microscope observations with electron back-scattering diffraction technique (SEM-EBSD) indicate that during deformation significant grain size reduction occurred, the average grain size reduced from about 250μm before deformation to about 50μm after deformation at temperatures from 300 C to 400°C, it reduced to about 100μm if deformed at above 400°C. The observed grain refinement at lower temperature and grain growth at higher temperature during the superplastic deformation is believed to be the result of the competing processes between dynamic recrystallization and dynamic grain growth, which are temperature and strain rate dependent. Transmission electron microscope (TEM) observations indicates that most of the grain boundaries are large-angle grain boundaries, though small amount of small-angle grain boundaries are also observed. The density of dislocations in the grains is very low in these superplasticlly deformed samples. It is evident that grain boundary played a role as the source and sink of the dislocation, being responsible for combined dislocation creep and diffusional creel. Therefore, the very large elongation obtained at the very high strain rates and high temperatures is attributed to dynamic dislocation hardening, recovery and recrystallization.
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Shibutani, Tadahiro, Qiang Yu, and Masaki Shiratori. "Evaluation of Creep Properties in Soldering Ball by Nanoindentation Creep." In ASME 2005 International Mechanical Engineering Congress and Exposition. ASMEDC, 2005. http://dx.doi.org/10.1115/imece2005-80160.

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In this paper, the behavior the behavior of creep deformation in low melting point alloy during a nanoindentation test was examined. Nanoindentation creep test was performed for eutectic tin-lead solder ball. Estimated creep exponent from the relationship between hardness and indenter dwell-time decreases as a function of time. The morphology of indented area shows that the transition from the deformation due to the tip in the early stage to another one in the last stage. Each grain near the indenter tip was transformed in the last stage. Stress analysis using a finite element method reveals that relaxation of equivalent stress progresses rapidly and the residual hydrostatic stress is dominant. Then, the gradient of the residual hydrostatic stress affects the chemical potential on grain boundaries and diffusion creep is activated. Therefore, the transition from the power-law creep to diffusion creep takes place during the nanoindentaion creep.
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Hua, F., C. M. Garner, H. G. Song, and J. W. Morris. "Creep Behavior of PB-Free Solders." In ASME 2001 International Mechanical Engineering Congress and Exposition. American Society of Mechanical Engineers, 2001. http://dx.doi.org/10.1115/imece2001/epp-24728.

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Abstract This study reports results of shear creep behavior of four Pb-free solders, Sn-3Ag-0.5Cu, Sn-3.5Ag, Sn-0.7Cu and Sn-10In-3.1Ag at 95θC and 130θC. At the stress levels tested, all the four solders showed the stress components close or larger than 5, typical for matrix creep. The calculated activation energies for Sn-0.7Cu, Sn-3.5Ag and Sn-3Ag-0.5Cu are from 103kJ/mol to 117kJ/mol, which are very close to the pure Sn self-diffusion activation energy (107kJ/mol). It suggested that the creep process is controlled by Sn bulk self-diffusion rate. The creep activation energy for Sn-10In-3.1Ag is higher in the range of 173–193kJ/mol. The Sn-0.7Cu, Sn-3Ag-0.5Cu and Sn-10In-3.1Ag solder joints were also prepared with two different cooling rates, 3.5θC/min. (furnace-cooling) and 2.7θC/S (air-cooling) and tested at 130θC. It was observed that faster cooled solder joints have faster creep strain rates than slower cooled solder joints at the stress levels tested for all three solders, due to the fine and even distribution of intermetallic particles.
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Reports on the topic "Diffusional Creep"

1

Cooper, Michael William Donald, K. A. Gamble, Christopher Matthews, and Anders David Ragnar Andersson. Irradiation enhanced diffusion and diffusional creep in U₃Si₂. Office of Scientific and Technical Information (OSTI), 2020. http://dx.doi.org/10.2172/1633555.

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McDeavitt, S. M., and A. A. Solomon. Hot-isostatic pressing of U-10Zr by grain boundary diffusion and creep cavitation. Part 2: Theory and data analysis. Office of Scientific and Technical Information (OSTI), 1997. http://dx.doi.org/10.2172/510397.

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Dorsch, J., and T. J. Katsube. Effective porosity and pore-throat sizes of mudrock saprolite from the Nolichucky Shale within Bear Creek Valley on the Oak Ridge Reservation: Implications for contaminant transport and retardation through matrix diffusion. Office of Scientific and Technical Information (OSTI), 1996. http://dx.doi.org/10.2172/285464.

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Final report. Paducah Gaseous Diffusion Plant PCB sediment survey: Big Bayou Creek and Little Bayou Creek, Paducah, Kentucky. Office of Scientific and Technical Information (OSTI), 1996. http://dx.doi.org/10.2172/766441.

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