990 resultados para intermediate band width manganites
Resumo:
The dynamic localization of saturated soil is investigated by considering the influence of higher strain gradient. It is shown that the strain gradient has a significant influence on the evolution of shear band in saturated soil and that the width of shear band is proportional to the square root of the strain gradient softening coefficient. The numerical simulation is processed to investigate the influences of shear strain gradient and other factors on the evolution of shear band.
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Table of Contents
width="20%">1 | width="70%">Introduction | width="10%" align="right">1 |
width="20%">1.1 | width="70%">What is an Adiabatic Shear Band? | width="10%" align="right">1 |
width="20%">1.2 | width="70%">The Importance of Adiabatic Shear Bands | width="10%" align="right">6 |
width="20%">1.3 | width="70%">Where Adiabatic Shear Bands Occur | width="10%" align="right">10 |
width="20%">1.4 | width="70%">Historical Aspects of Shear Bands | width="10%" align="right">11 |
width="20%">1.5 | width="70%">Adiabatic Shear Bands and Fracture Maps | width="10%" align="right">14 |
width="20%">1.6 | width="70%">Scope of the Book | width="10%" align="right">20 |
width="20%">2 | width="70%">Characteristic Aspects of Adiabatic Shear Bands | width="10%" align="right">24 |
width="20%">2.1 | width="70%">General Features | width="10%" align="right">24 |
width="20%">2.2 | width="70%">Deformed Bands | width="10%" align="right">27 |
width="20%">2.3 | width="70%">Transformed Bands | width="10%" align="right">28 |
width="20%">2.4 | width="70%">Variables Relevant to Adiabatic Shear Banding | width="10%" align="right">35 |
width="20%">2.5 | width="70%">Adiabatic Shear Bands in Non-Metals | width="10%" align="right">44 |
width="20%">3 | width="70%">Fracture and Damage Related to Adiabatic Shear Bands | width="10%" align="right">54 |
width="20%">3.1 | width="70%">Adiabatic Shear Band Induced Fracture | width="10%" align="right">54 |
width="20%">3.2 | width="70%">Microscopic Damage in Adiabatic Shear Bands | width="10%" align="right">57 |
width="20%">3.3 | width="70%">Metallurgical Implications | width="10%" align="right">69 |
width="20%">3.4 | width="70%">Effects of Stress State | width="10%" align="right">73 |
width="20%">4 | width="70%">Testing Methods | width="10%" align="right">76 |
width="20%">4.1 | width="70%">General Requirements and Remarks | width="10%" align="right">76 |
width="20%">4.2 | width="70%">Dynamic Torsion Tests | width="10%" align="right">80 |
width="20%">4.3 | width="70%">Dynamic Compression Tests | width="10%" align="right">91 |
width="20%">4.4 | width="70%">Contained Cylinder Tests | width="10%" align="right">95 |
width="20%">4.5 | width="70%">Transient Measurements | width="10%" align="right">98 |
width="20%">5 | width="70%">Constitutive Equations | width="10%" align="right">104 |
width="20%">5.1 | width="70%">Effect of Strain Rate on Stress-Strain Behaviour | width="10%" align="right">104 |
width="20%">5.2 | width="70%">Strain-Rate History Effects | width="10%" align="right">110 |
width="20%">5.3 | width="70%">Effect of Temperature on Stress-Strain Behaviour | width="10%" align="right">114 |
width="20%">5.4 | width="70%">Constitutive Equations for Non-Metals | width="10%" align="right">124 |
width="20%">6 | width="70%">Occurrence of Adiabatic Shear Bands | width="10%" align="right">125 |
width="20%">6.1 | width="70%">Empirical Criteria | width="10%" align="right">125 |
width="20%">6.2 | width="70%">One-Dimensional Equations and Linear Instability Analysis | width="10%" align="right">134 |
width="20%">6.3 | width="70%">Localization Analysis | width="10%" align="right">140 |
width="20%">6.4 | width="70%">Experimental Verification | width="10%" align="right">146 |
width="20%">7 | width="70%">Formation and Evolution of Shear Bands | width="10%" align="right">155 |
width="20%">7.1 | width="70%">Post-Instability Phenomena | width="10%" align="right">156 |
width="20%">7.2 | width="70%">Scaling and Approximations | width="10%" align="right">162 |
width="20%">7.3 | width="70%">Wave Trapping and Viscous Dissipation | width="10%" align="right">167 |
width="20%">7.4 | width="70%">The Intermediate Stage and the Formation of Adiabatic Shear Bands | width="10%" align="right">171 |
width="20%">7.5 | width="70%">Late Stage Behaviour and Post-Mortem Morphology | width="10%" align="right">179 |
width="20%">7.6 | width="70%">Adiabatic Shear Bands in Multi-Dimensional Stress States | width="10%" align="right">187 |
width="20%">8 | width="70%">Numerical Studies of Adiabatic Shear Bands | width="10%" align="right">194 |
width="20%">8.1 | width="70%">Objects, Problems and Techniques Involved in Numerical Simulations | width="10%" align="right">194 |
width="20%">8.2 | width="70%">One-Dimensional Simulation of Adiabatic Shear Banding | width="10%" align="right">199 |
width="20%">8.3 | width="70%">Simulation with Adaptive Finite Element Methods | width="10%" align="right">213 |
width="20%">8.4 | width="70%">Adiabatic Shear Bands in the Plane Strain Stress State | width="10%" align="right">218 |
width="20%">9 | width="70%">Selected Topics in Impact Dynamics | width="10%" align="right">229 |
width="20%">9.1 | width="70%">Planar Impact | width="10%" align="right">230 |
width="20%">9.2 | width="70%">Fragmentation | width="10%" align="right">237 |
width="20%">9.3 | width="70%">Penetration | width="10%" align="right">244 |
width="20%">9.4 | width="70%">Erosion | width="10%" align="right">255 |
width="20%">9.5 | width="70%">Ignition of Explosives | width="10%" align="right">261 |
width="20%">9.6 | width="70%">Explosive Welding | width="10%" align="right">268 |
width="20%">10 | width="70%">Selected Topics in Metalworking | width="10%" align="right">273 |
width="20%">10.1 | width="70%">Classification of Processes | width="10%" align="right">273 |
width="20%">10.2 | width="70%">Upsetting | width="10%" align="right">276 |
width="20%">10.3 | width="70%">Metalcutting | width="10%" align="right">286 |
width="20%">10.4 | width="70%">Blanking | width="10%" align="right">293 |
width="20%"> | width="70%">Appendices | width="10%" align="right">297 |
width="20%">A | width="70%">Quick Reference | width="10%" align="right">298 |
width="20%">B | width="70%">Specific Heat and Thermal Conductivity | width="10%" align="right">301 |
width="20%">C | width="70%">Thermal Softening and Related Temperature Dependence | width="10%" align="right">312 |
width="20%">D | width="70%">Materials Showing Adiabatic Shear Bands | width="10%" align="right">335 |
width="20%">E | width="70%">Specification of Selected Materials Showing Adiabatic Shear Bands | width="10%" align="right">341 |
width="20%">F | width="70%">Conversion Factors | width="10%" align="right">357 |
width="20%"> | width="70%">References | width="10%" align="right">358 |
width="20%"> | width="70%">Author Index | width="10%" align="right">369 |
width="20%"> | width="70%">Subject Index | width="10%" align="right">375 |
Resumo:
Cladding band structure of air-guiding photonic crystal fibers with high air-filling fraction is calculated in terms of fiber shape variation. The fundamental photonic band gap dependence on structure parameters, air-filling fraction and spacing, is also investigated. The numerical results show that the band gap edges shift toward longer wavelength as the air-filling fraction is increased, whereas the relative band gap width increases linearly. For a fixed air-filling fraction, the band gap edges with respect to spacing keep constant. With this method, the simulation results agree well with the reported data. © 2007 Elsevier B.V. All rights reserved.
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The characteristics of the cladding band structure of air-core photonic crystal fibers with silica rings in triangular lattice are investigated by using a standard plane wave method. The numerical results show that light can be localized in the air core by the photonic band gaps of the fiber. By increasing the air-filling fraction, the band gap edges of the low frequency photonic band gaps shift to shorter wavelength.. whereas the band gap width decreases linearly. In order to make a specified light fall in the low frequency band gaps of the fiber, the interplay of the silica ring spacing and the air-filling fraction is also analyzed. It shows that the silica ring spacing increases monotonously when the air-filling fraction is increased, and the spacing range increases exponentially. This type fiber might have potential in infrared light transmission. (c) 2006 Elsevier B.V. All rights reserved.
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At high Reynolds numbers, wake flows become more globally unstable when they are confined within a duct or between two flat plates. At Reynolds numbers around 100, however, global analyses suggest that such flows become more stable when confined, while local analyses suggest that they become more unstable. The aim of this paper is to resolve this apparent contradiction by examining a set of obstacle-free wakes. In this theoretical and numerical study, we combine global and local stability analyses of planar wake flows at $\mathit{Re}= 100$ to determine the effect of confinement. We find that confinement acts in three ways: it modifies the length of the recirculation zone if one exists, it brings the boundary layers closer to the shear layers, and it can make the flow more locally absolutely unstable. Depending on the flow parameters, these effects work with or against each other to destabilize or stabilize the flow. In wake flows at $\mathit{Re}= 100$ with free-slip boundaries, flows are most globally unstable when the outer flows are 50 % wider than the half-width of the inner flow because the first and third effects work together. In wake flows at $\mathit{Re}= 100$ with no-slip boundaries, confinement has little overall effect when the flows are weakly confined because the first two effects work against the third. Confinement has a strong stabilizing effect, however, when the flows are strongly confined because all three effects work together. By combining local and global analyses, we have been able to isolate these three effects and resolve the apparent contradictions in previous work.
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Surface states in semiconductor nanowires (NWs) are detrimental to the NW optical and electronic properties and to their light emission-based applications, due to the large surface-to-volume ratio of NWs and the congregation of defects states near surfaces. In this paper, we demonstrated an effective approach to eliminate surface states in InAs NWs of zinc-blende (ZB) and wurtzite (WZ) structures and a dramatic recovery of band edge emission through surface passivation with organic sulfide octadecylthiol (ODT). Microphotoluminescence (PL) measurements were carried out before and after passivation to study the dominant recombination mechanisms and surface state densities of the NWs. For WZ-NWs, we show that the passivation removed the surface states and recovered the band-edge emission, leading to a factor of ∼19 reduction of PL linewidth. For ZB-NWs, the deep surface states were removed and the PL peaks width became as narrow as ∼250 nm with some remaining emission of near band-edge surface states. The passivated NWs showed excellent stability in atmosphere, water, and heat environments. In particular, no observable changes occurred in the PL features from the passivated NWs exposed in air for more than five months.
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The monovalent potassium doped manganites Pr0.6Sr 0.4-xKxMnO3 (x = 0.05-0.2) are characterized using the complementary magnetic susceptibility and electron resonance methods. In paramagnetic phase the temperature variations of the inverse magnetic susceptibility and the inverse intensity of resonance signal obey the Curie-Weiss law. A similarity in temperature variation of resonance signal width and the adiabatic polaron conductivity points to the polaron mechanism controlling the resonance linewidth. The low temperature limit of the pure paramagnetic phase is determined from the electron resonance spectra revealing the mixed phase spread down to the Curie temperature. © 2013 Elsevier B.V. All rights reserved.
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Optimized AlGaN/AlN/GaN high electron mobility transistor (HEMT) with high mobility GaN channel layer structures were grown on 2-in. diameter semi-insulating 6H-SiC substrates by MOCVD. The 2-in. diameter GaN HEMT wafer exhibited a low average sheet resistance of 261.9 Omega/square, with the resistance un-uniformity as low as 2.23%. Atomic force microscopy measurements revealed a smooth AlGaN surface whose root-mean-square roughness is 0.281 nm for a scan area of 5 x 5 mu m. For the single-cell HEMTs device of 2.5-mm gate width fabricated using the materials, a maximum drain current density of 1.31 A/mm, an extrinsic transconductance of 450 mS/mm, a current gain cutoff frequency of 24 GHz and a maximum frequency of oscillation 54 GHz were achieved. The four-cell internally-matched GaN HEMTs device with 10-mm total gate width demonstrated a very high output power of 45.2 W at 8 GHz under the condition of continuous-wave (CW), with a power added efficiency of 32.0% and power gain of 6.2 dB. To our best knowledge, the achieved output power of internally-matched devices are the state-of-the-art result ever reported for X-band GaN-based HEMTs. Crown Copyright (C) 2009 Published by Elsevier Ltd. All rights reserved.
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In this paper we present a novel growth of grade-strained bulk InGaAs/InP by linearly changing group-III TMGa source flow during low-pressure metalorganic vapor-phase epitaxy (LP-MOVPE). The high-resolution X-ray diffraction (HRXRD) measurements showed that much different strain was simultaneously introduced into the fabricated bulk InGaAs/InP by utilizing this novel growth method. We experimentally demonstrated the utility and simplicity of the growth method by fabricating common laser diodes. As a first step, under the injection current of 100 mA, a more flat gain curve which has a spectral full-width at half-maximum (FWHM) of about 120 nm was achieved by using the presented growth technique. Our experimental results show that the simple and new growth method is very suitable for fabricating broad-band semiconductor optoelectronic devices. (C) 2003 Elsevier B.V. All rights reserved.
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In the optical network, the quick and accurate alignment with wavelength is an important issue during the channel detection. At this point, a filter having flat-top response characteristic is an effective solution. Based on multiple-step-type Fabry-Perot cavity structure, a novel all-Si-based thermooptical tunable flat-top filter with narrow-band has been fabricated, using our patent silicon-on-reflector bonding technology. The device demonstrated a 1-dB flat-top width of 1 nm, 3-dB band of 3 nm, free spectra range of 8 nm, and the tuning range of 4.6 nm was obtained under the applied voltage of 4 V.
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Based on the band anticrossing model, the effects of the strain-compensated layer and the strain-mediated layer on the band structure, gain and differential gain of GaInNAs/GaAs quantum well lasers have been investigated. The results show that the GaNAs barrier has a disadvantage in increasing the density of states in the conduction band. Meanwhile, the multilayer quantum wells need higher transparency carrier density than the GaInNAs/GaAs single quantum well with the same wavelength. However, they help to suppress the degradation of the differential gain. The calculation also shows that from the viewpoint of band structure, the strain-compensated structure and the strain-mediated structure have similar features.
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High-quality GaN epilayers were grown on Si (1 1 1) substrate by metalorganic chemical vapor deposition. The growth process was featured by using an ultrathin AlN wetting layer (WL) in combination with a low-temperature (LT) GaN nucleation layer (NL). The full-width at half-maximum (FWHM) of the X-ray rocking curve for the GaN (0 0 0 2) diffraction was 15 arcmin. The dislocation density estimated from TEM investigation was found to be of the order of 10(9)cm(-2). The FWHM of the dominant band edge emission peak of the GaN was measured to be 47 meV by photoluminescence measurement at room temperature. The ultrathin AlN WL was produced by nitridation of the aluminium pre-covered substrate surface. The reflection high-energy electron diffraction showed that the AlN WL was wurtzite and the surface morphology was like the nitridated surface of sapphire by the atomic force microscopy measurement. X-ray photoelectron spectroscopy measurement showed that Si and SixNy at a certain concentration were intermixed in the AlN WL. This study suggests that by employing an appropriate WL combined with a LT NL, high-quality heteroepitaxy is achievable even with large mismatch. (C) 2002 Elsevier Science B.V. All rights reserved.
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Gallium nitride (GaN)-based Schottky junctions were fabricated by RF-plasma-assisted molecular beam epitaxy (MBE). The GaN epitaxial layers were deposited on novel double buffer layers that consist of a conventional low-temperature buffer layer (LTBL) grown at 500 degreesC and an intermediate-temperature buffer layer (ITBL) deposited at 690 degreesC. Low-frequency excess noise and deep level transient Fourier spectroscopy (DLTFS) were measured from the devices. The results demonstrate a significant reduction in the density of deep levels in the devices fabricated with the GaN films grown with an ITBL. Compared to the control sample, which was grown with just a conventional LTBL, a three-order-of-magnitude reduction in the deep levels 0.4 eV below the conduction band minimum (Ec) is observed in the bulk of the thin films using DLTFS measurements.
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Wurtzite GaN films have been grown on (001) Si substrates using gamma-Al2O3 as an intermediate layer by low pressure (similar to 76 Torr) metalorganic chemical vapor deposition. Reflection high energy electron diffraction and double crystal x-ray diffraction measurements revealed that the thin gamma-Al2O3 layer of "compliant" character was an effective intermediate layer for the GaN film grown epitaxially on Si. The narrowest linewidth of the x-ray rocking curve for (0002) diffraction of the 1.3 mu m GaN sample was 54 arcmin. The orientation relationship of GaN/gamma-Al2O3/Si was (0001) GaN parallel to(001) gamma-Al2O3 parallel to(001) Si, [11-20] GaN parallel to[110] gamma-Al2O3 parallel to[110] Si. The photoluminescence measurement for GaN at room temperature exhibited a near band-edge peak of 365 nm (3.4 eV). (C) 1998 American Institute of Physics.
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The exciton states in isolated and semi-isolated quantum wires are studied. It is found that the image charges have a large effect on the effective Coulomb potential in wires. For the isolated wire the effective potential approaches the Coulomb potential in vacuum at large z distance. For the semi-isolated wire the effective potential is intermediate between the Coulomb potential in vacuum and the screened Coulomb potential at large distance. The exciton binding energy in the isolated wire is about ten times larger than that in the quantum well, and that in the semi-isolated wire is also intermediate between those in the isolated wire and in the quantum well. When the lateral width increases the binding energy decreases further, and approaches that in the quantum well. The real valence-band structure is taken into account, the exciton wave functions of the ground state in the zero-order approximation are given, and the reduced mass is calculated. The effect of the coupling between the ground and excited states are considered by the degenerate perturbation method, and it is found the coupling effect is small compared to the binding energy.