Interval Evaluations in the Analytic Hierarchy Process By Possibility Analysis

Since a pairwise comparison matrix in the Analytic Hierarchy Process (AHP) is based on human intuition, the given matrix will always include inconsistent elements violating the transitivity property. We propose the Interval AHP by which interval weights can be obtained. The widths of the estimated interval weights represent inconsistency in judging data. Since interval weights can be obtained from inconsistent data, the proposed Interval AHP is more appropriate to human judgment. Assuming crisp values in a pairwise comparison matrix, the interval comparisons including the given crisp comparisons can be obtained by applying the Linear Programming (LP) approach. Using an interval preference relation, the Interval AHP for crisp data can be extended to an approach for interval data allowing to express the uncertainty of human judgment in pairwise comparisons.     

Nonsingular BEM formulations for thin-walled structures and elastostatic crack problems

Summary This paper presents a unique approach, named mathematical regularization, to remove the nearly-singular and singular integrals occurring in the boundary integral formulations for the solution of the boundary value problems with a pathologica integration boundary due to the very near or coinciding parts of the total boundary. Nonsingular boundary integral equations are derived for thin-walled structure problems. In the case of crack-like problems, we present two kinds of the nonsingular integral representations of the secondary fields and the derivative boundary integral equations.     

Evaluation of size effect on mechanical properties of singlecrystal silicon by nanoscale bending test using AFM

This paper describes a nanometer-scale bending test for a single crystal silicon (Si) fixed beam using an atomic force microscope (AFM). This research focuses on revealing the size effect on the mechanical property of Si beams ranging from a nano- to millimeter scale. Nanometer-scale Si beams, with widths from 200 to 800 nm and a thickness of 255 nm, were fabricated on an Si diaphragm by means of field-enhanced anodization using AFM and anisotropic wet etching. The efficient condition of the field-enhanced anodization could be obtained by changing the bias voltage and the scanning speed of the cantilever. Bending tests for micro- and millimeter-scale Si beams fabricated by a photolithography technique were also carried out using an ultraprecision hardness tester and scratch tester, respectively. Comparisons of Young's modulus and bending strength, of Si among the nano-, micro-, and millimeter scales showed that the specimen size did not have an influence on the Young's modulus in the (110) direction, whereas it produced a large effect on the bending strength. Observations of the fractured surface and calculations of the clack length from Griffith's theory made it clear that the maximum peak-to-valley distance of specimen surface caused the size effect on the bending strength     

Effects of plastic strain amplitudes on non-proportional cyclic plasticity

Summary A series of plastic strain controlled cyclic tests was performed to facilitate the modelling of cyclic plasticity under general multiaxial loading conditions. The tests were carried out by applying combined axial force and torque to thin-walled tubular specimens of type 316 stainless steel at room temperature. Torsional and circular cycles of the equivalent plastic strain amplitude (von Mises type) ofe ^p /2=0.1, 0.2 and 0.4% were specified.The results showed that the cyclic hardening under the circular cycles is 1.5–1.8 times as large as that under the torsional cycles of the same value ofe ^p /2 in the saturated state. It was also observed that, in the case of torsional cycles, these saturated values are not affected by the sequence of plastic strain cycles in the past, while in the case of circular cycles, they are affected by the cycles of larger amplitudes. Furthermore, it was elucidated that this memory effect depends only on the cycles of the largest amplitude in the past.With 12 Figures     

Delayed retardation phenomena of fatigue crack growth in various steels and alloys

The delayed retardation phenomena of fatigue crack growth resulting from a single application of overload were investigated for five steels, two aluminium alloys and a titanium alloy. As long as the small scale yielding condition was satisfied at the overloaded crack tips, the retardation behaviour of these materials was expressed consistently by four parameters; the peak/baseline stress ratio, r, the exponent in the Paris equation, m, the overload-affected zone size, _D, and the crack distance at the minimum rate of crack growth, _B. Then the parameters, _B and _D, characterizing the retardation phenomena for these materials were determined. The retardation of aluminium alloys was stronger than that of the other materials. This is attributed to the lower value of _B/ _D in aluminium alloys than in the other materials. In the case of r=2, the overload-affected zone sizes, _D, were nearly equal to 1.5 ₀ in HT80 steel and aluminium alloys, slightly lower than 1.5 ₀ in SNCM8 steel and much larger than 1.5 ₀ in A553 steel and the titanium alloy, where ₀ is the monotonic plastic zone size calculated according to the Dugdale model. The dependence of retardation on baseline stress intensity, K ₁, appeared somewhat complicated. In the cases of A553 steel and A2017 aluminium alloy the amount of retardation increased with increasing K ₁ value, while in the cases of HT80 steel and Ti-6A1-4V titanium alloy the tendency appeared in the reverse direction. The former behaviour was related to the change in the stress state from plane strain to plane stress at the overloaded crack tips and the latter was related to the threshold of stress intensity.     

The cyclicJ-integral as a criterion for fatigue crack growth

The definition of the cyclic J-integral is offered and its physical significance for fatigue crack growth is discussed using the Dugdale model on the assumption that the crack closure, cycle dependent creep deformation, and crack extension under cycling can be neglected. It is shown that the cyclic J-integral for small scale yielding is equivalent to theJ-integral for linear elastic crack independent of loading processes, while the value for large scale yielding varies with the loading processes. However, in both cases, the cyclicJ-integral remains constant during the reversal of loading under a constant stress range, if the first monotonic loading stage is excluded. In this situation, the cyclicJ-integral can be applied as a criterion for fatigue crack growth, since it is evaluated as a generalized force on dislocations to be moved or the energy flow rate to be dissipated to heat by the dislocation movements in an element just attached to the fatigued crack tip during one cycle of loading. It is suggested that the available experimental data of different materials for fatigue crack growth can be generalized to a unified formulation on the basis of the energy criterion. It is also deduced that the threshold J corresponding to K _th should be larger than 4 where is the surface energy of the material. Finally the operational definition of the cyclicJ-integral on single loadversus displacement curves is given for center cracked plate with wide uncracked ligaments in tension.

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Résumé On présente la définition de l'intégrale J cyclique et sa signification physique dans le cas d'une croissance de fissure de fatigue est discutée en utilisant le modèle de Dugdale et l'hypothèse que la fermeture de la fissure, la déformation de fluage liée au cycle, et l'extension de la fissure au cours du cycle peuvent être négligées. On montre que l'intégraleJ cyclique est, dans le cas d'écoulement plastique à faible échelle, équivalente à l'intégraleJ utilisée pour les fissures élastiques linéaires indépendamment des processus de mise en charge, tandis que la valeur de déformation plastique macroscopique varie avec le processus de mise en charge. Cependant, dans les 2 cas, l'intégraleJ cyclique demeure constante au cours du renversement de charge appliquée à tension constante si l'on exclut le premier stade de mise en charge monotone. Dans cette situation, l'intégraleJ cyclique peut être appliquée comme critère de la croissance d'une fissure de fatigue puisqu'elle représente une forme généralisée de force, un effort sur les dislocations à mouvoir ou à l'écoulement d'énergie dissipée en chaleur par les mouvements de dislocation dans un élément immédiatement solidaire de l'extrémité de la fissure de fatigue, au cours d'un cycle de mise en charge. On suggère que les données expérimentales disponibles sur différents matériaux pour la croissance d'une fissure de fatigue puissent être généralisées à une formulation unifiée, sur base d'un critère d'énergie. On déduit également que le seuil J correspondant à K _th devrait être plus grand que 4, où est l'énergie de surface du matériau. Finalement, la définition opérationnelle de l'intégraleJ cyclique sous simple charge en fonction des courbes de déplacement est fournie dans le cas d'une plaque comportant une fissure centrale et de larges ligaments non fissurés, soumises à traction.

     

Delayed hypersensitivity in untreated patients with Hodgkin''s disease--with special reference to small lymphocyte counts in the blood

A hundred and thirty patients have been treated with Amitriptylin in the "Clinique de Psychiatrie" in Marseille during the last eight years. The review of the hundred cases for which the information are the most detailed show that Amitriptylin remains one of the most powerful, manageable and well-tolerated anti-depressant drugs available at the present time. Its therapeutic indications are numerous, but the best ones are proceeding from depressed states with high anxious participation in subjects of less that 60 years of age.     

Orientation dependence of fracture toughness measured by indentation methods and its relation to surface energy in single crystal silicon

Fracture toughness of silicon crystals has been investigated using indentation methods, and their surface energies have been calculated by molecular dynamics (MD). In order to determine the most preferential fracture plane at room temperature among the crystallographic planes containing the 〈001〉, 〈110〉 and 〈111〉 directions, a conical indenter was forced into (001), (110) and (111) silicon wafers at room temperature. Dominant {110}, {111} and {110} cracks were introduced from the indents on (001), (011) and (111) wafers, respectively. Fracture occurs most easily along {110}, {111} and {110} planes among the crystallographic planes containing the 〈001〉, 〈011〉 and 〈111〉 directions, respectively. A series of surface energies of those planes were calculated by MD to confirm the orientation dependence of fracture toughness. The surface energy of the {110} plane is the minimum of 1.50 Jm⁻² among planes containing the 〈001〉 and 〈111〉 directions, respectively, and that of the {111} plane is the minimum of 1.19 Jm⁻² among the planes containing the 〈011〉 direction. Fracture toughness of those planes was also derived from the calculated surface energies. It was shown that the K _IC value of the {110} crack plane was the minimum among those for the planes containing the 〈001〉 and 〈111〉 directions, respectively, and that K _IC value of the {111} crack plane was the minimum among those for the planes containing the 〈011〉 direction. These results are in good agreement with that obtained conical indentation.     

Construction of ULT-MRI cryostat for ultra low temperature physics

No Heading We have constructed an Ultra Low Temperature cryostat for Magnetic Resonance Imaging (ULT-MRI) applicable for various condensed phases of ³He at ultra low temperature, such as Nuclear Ordered Solid ³He or superfluid ³He. In contrast to conventional MRI for general use, where a pulsed-field gradient method is commonly used, we used a steady-field gradient method to avoid eddy current heating to metal parts at ultra low temperature. To avoid nonlinear response from the nuclear ordered spin system, which contradicts a principle of conventional MRI, we employed Free Induction Decay (FID) after a small tipping angle RF pulse to obtain the spectrum.PACS numbers: 07.20Mc, 67.57.Lm, 67.80.Jd, 76.60.Pc, 83.85.Fg