1,725,215 research outputs found
CB-5083-resistant MV4-11 cells exhibit features of permanent endoplasmic reticulum (ER) stress but no apoptosis.
No full text(A) Immunoblot showing induction of ER stress in inhibitor-resistant cells after a few months of continuous treatment with 200 and 500 nM CB-5083. (B and C) Flow cytometry analysis using Annexin V and 7-AAD staining showed decreased apoptosis in CB-5083-resistant cell lines. (D and E) IC50 values for CB-5083 in the indicated cell lines upon withdrawal and re-treatment with CB-5083. (F) Analysis of the coding sequence of VCP identified a variant (c.1591C>A p.I531L) in the cell line treated with 1 μM CB-5083.</p
Potential fatigue strength improvement of AA 5083-H111 notched parts by wire brush hammering: Experimental analysis and numerical simulation
Get PDFThe effects of milling as machining process and a post-machining treatment by wire-brush hammering, on the near surface layer characteristics of AA 5083-H111 were investigated. Surface texture, work-hardening and residual stress profiles were determined by roughness measurement, scanning electron microscope (SEM) examinations, microhardness and X-ray diffraction (XRD) measurements. The effects of surface preparation on the fatigue strength were assessed by bending fatigue tests performed on notched samples for two loading stress ratios R0.1 and R0.5. It is found that the bending fatigue limit at R0.1 and 107 cycles is 20% increased, with respect to the machined surface, by wire-brush hammering. This improvement was discussed on the basis of the role of surface topography, stabilized residual stress and work-hardening on the fatigue-crack network nucleation and growth. The effects biaxial residual stress field and surface work-hardening were taken into account in the finite element model. A multi-axial fatigue criterion was proposed to predict the fatigue strength of aluminum alloy notched parts for both machined and treated states
Comparing the Corrosion Resistance of 5083 Al and Al2O33D/5083 Al Composite in a Chloride Environment
No full textIn this study, an Al2O33D/5083 Al composite was fabricated by infiltrating a molten 5083 Al alloy into a three-dimensional alumina reticulated porosity ceramics skeleton preform (Al2O33D) using a pressureless infiltration method. The corrosion resistance of 5083 Al alloy and Al2O33D/5083 Al in NaCl solution were compared via electrochemical impedance spectroscopy (EIS), dynamic polarization potential (PDP), and neutral salt spray (NSS) tests. The microstructure of the two materials were investigated by 3D X-ray microscope and scanning electron microscopy aiming at understanding the corrosion mechanisms. Results show that an Al2O33D/5083 Al composite consists of interpenetrating structure of 3D-continuous matrices of continuous networks 5083 Al alloy and Al2O33D phase. A large area of strong interfaces of 5083 Al and Al2O33D exist in the Al2O33D/5083 Al composite. The corrosion development process can be divided into the initial period, the development period, and the stability period. Al2O33D used as reinforcement in Al2O33D/5083 Al composite improves the corrosion resistance of Al2O33D/5083 Al composite via electrochemistry tests. Thus, the corrosion resistance of Al2O33D/5083 Al is higher than that of 5083 Al alloy. The NSS test results indicate that the corrosion resistance of Al2O33D/5083 Al was lower than that of 5083 Al alloy during the initial period, higher than that of 5083 Al alloy during the development period, and there was no obvious difference in corrosion resistance during the stability period. It is considered that the elements in 5083 Al alloy infiltrated into the Al2O33D/5083 Al composite are segregated, and the uniform distribution of the segregated elements leads to galvanic corrosion during the corrosion initial period. The perfect combination of interfaces of Al2O33D and the 5083 Al alloy matrix promotes excellent corrosion resistance during the stability period
Crack opening behavior in aluminum alloy 5083
No full textFatigue life is the summation of crack initiation life and propogation life, but the technique to evaluate initiation and propogation of the crack by a unified theorem has not been established yet. Toyosada et al. proposed a fatigue crack propogation law based on re-tensile plastic zone's generated load (RPG load). Moreover, they established a simulation code for analyzing fatigue crack propogation behavior in various aluminium alloys. An investigation is necessary to check the crack opening behavior in case of both experiment and simulation for each aluminium alloy, before conducting estimation of fatigue crack propogation behaviour in aluminium alloys. In this study, the crack opening profiles in aluminium alloy 5083 were estimated by Dugdale Model and these profiles were compared with those by experiments and FEM subject to CCT specimen and a coefficient, called plastic constraint factor was introduced, which should be applied to Dugdale Model to achieve improved crack opening profile in aluminium allo
Baltimore & Ohio (B&O) 5083
No full textA photograph print showing Baltimore & Ohio (B&O) 5083, 4-6-2, Washington, D.C
Fatigue Crack Growth and Fracture Toughness in Bimodal Al 5083
No full textABSTRACTThe fatigue crack growth rates and fracture toughness of bulk nanocrystalline Al 5083 having a bimodal grain size distribution were investigated. The nanocrystalline powders were prepared by mechanically ball milling spray atomized Al 5083 powders in liquid nitrogen. This nanocrystalline powder was blended with 50 wt% spray atomized large grained Al 5083 powders. The blended powder was then cold pressed, degassed, and extruded into rods. The bimodal Al 5083 thus produced consists of nanocrystalline grain bands and coarse grain bands. While the yield strength of the bimodal Al 5083 is about 25% lower than that of the all nanocrystalline Al 5083, its tensile ductility is almost 50% greater. In addition, the fracture toughness of the bimodal material is about 85% higher than that of the all nanocrystalline counterpart. Fatigue crack growth rates of bimodal Al 5083 are about 30% lower than those of all nanocrystalline Al 5083. The lower fatigue crack growth rates are accompanied by more tortuous crack paths when the crack propagated through the coarse grain regions in the bimodal Al 5083.</jats:p
Union Pacific (UP) 5083 & 9078
No full textA photograph postcard showing Union Pacific (UP) 5083, 2-10-2, and 9078, 4-12-2, on westbound freight extra, near Granite Canyon, WY, 87 cars, 20mph
B4C/5083 Al Composite Prepared by Cryomilling
No full textIn the present investigation, the composite powder with 20wt.% particulate B4C and 80wt.% nanocrystalline 5083 Al was fabricated using mechanically milling at cryogenic temperature (cryomilling). After this, the cryomilled composite powder was homogeneously blended with an equal amount of unmilled coarse-grained 5083 Al. The blended powder was consolidated with hot-pressing at 500°C, followed by hot extrusion at 410°C. The consolidated composite consists of 10wt.% B4C, 50wt.% coarse grain 5083 Al and the balance nanocrystalline 5083 Al. The microstructure evolution of the composite during cryomilling and consolidation was investigated by X-ray diffraction (XRD), optical microscopy (OM) and scanning electron microscopy (SEM). The results show that the particle size of the cryomilled composite powder became smaller and then bigger with milling time longer. This demonstrates the course rely mainly on broken first, and then rely mainly on cold welding with milling time longer. B4C particles can be distributed in 5083 Al matrix uniformly. In addition, the presence of oxygen and nitrogen in cryomilled powders has been demonstrated in this paper.</jats:p
Union Pacific (UP) 3912 & 5083
No full textA photograph postcard showing Union Pacific (UP) 3912, 4-6-6-4, on eastbound freight extra, with 5083, 2-10-2, pushing on rear, near Gateway, UT, 11 miles east of Ogden, UT, 77 cars, 25 mph
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