Relevant bibliographies by topics / Facture toughness; Crack growth

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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 'Facture toughness; Crack growth'

Author: Grafiati
Published: 4 June 2021
Last updated: 16 February 2022

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Journal articles on the topic "Facture toughness; Crack growth"

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Kuang, Jia Cai, Hong Lei Wang, Xin Gui Zhou, and Ying Jun Deng. "Fracture Toughness of CNTs/AlN Ceramics Tested by Indentation." Advanced Materials Research 177 (December 2010): 151–53. http://dx.doi.org/10.4028/www.scientific.net/amr.177.151.

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CNTs/AlN ceramics were fabricated by hot-pressing sintering process. The fracture toughness was measured by indentation method. The morphologies of indentation cracks were analyzed by SEM. The results show that the facture toughness of AlN was slightly improved because appreciate toughening mechanisms such as CNTs pull-out, crack bridging and deflect operate in CNTs/AlN. In addition, the facture toughness of CNTs/AlN increased with increasing CNTs content up to 3wt%. Then, the fracture toughness decrease when the CNTs content is 4wt%.
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Blugan, Gurdial, Richard Dobedoe, I. Gee, Nina Orlovskaya, and Jakob Kübler. "Failure Behaviour of High Toughness Multi-Layer Si3N4 and Si3N4-TiN Based Laminates." Key Engineering Materials 290 (July 2005): 175–82. http://dx.doi.org/10.4028/www.scientific.net/kem.290.175.

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Multi-layer laminates were produced using alternating layers of Si3N4 and Si3N4+TiN. The differences in the coefficient of thermal expansions between the alternating layers lead to residual stresses after cooling. These are compressive in the Si3N4 layers and tensile in the Si3N4+TiN layers. The existence of these stresses in the laminates effect the crack propagation behaviour during failure. Different designs of laminates were produced with external layers under compression and tension exhibiting different failure mechanisms. Facture toughness was measured by SEVNB method. In systems with external layers under compression the measured fracture toughness was up to three times that of Si3N4, i.e. up to 17 MPa m1/2. In systems with external layers under tension during failure the energy absorbing effects of crack deflection and crack bifurcation were obtained. High temperature tests were performed to determine the onset temperature for residual stresses in these laminates. Micro-laminates with compressive layers of only 30 µm thickness with high strength and fracture toughness and were manufactured.
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Suresh, S., and A. K. Vasudevan. "On the relationship between crack initiation toughness and crack growth toughness." Materials Science and Engineering 79, no. 2 (May 1986): 183–90. http://dx.doi.org/10.1016/0025-5416(86)90403-9.

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Gu, Inhoy. "Crack-Tip-Acuity Effect on Crack Growth Initiation." Journal of Engineering Materials and Technology 109, no. 3 (July 1, 1987): 216–20. http://dx.doi.org/10.1115/1.3225966.

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For a stationary crack of an initially finite root radius in plane-strain tension, the strain fields around the smoothly blunted crack-tip are calculated for each deformation stage using the slipline field method for nonhardening plastic material. The crack growth initiation from the blunt crack-tip in small-scale yielding, with a full triaxiality ahead of the crack-line, is predicted based on the fracture criterion of the fracture strain at a characteristic distance, obtained by applying the criterion to the case of a sharp crack-tip, in which the effect of the initial root radius on the strain distribution can be neglected. The predicted toughness for mild steel is in reasonable agreement with an experiment. For other materials, the observed J-integral value at fracture initiation, consistent with the present analysis, increases linearly with the initial root radius, but its rate shows a large deviation from the model, which is discussed due to the shear band development. The analysis also predicts that the toughness of a cracked low-ductility material does not increase by making the initial crack-root profile round, and that the reduced triaxiality at the crack-tip brings about a toughness increase.
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Qi, Hong Yu, Xiao Guang Yang, and Rui Li. "Interfacial Fracture Toughness of APS Thermal Barrier Coating under High Temperature." Key Engineering Materials 348-349 (September 2007): 181–84. http://dx.doi.org/10.4028/www.scientific.net/kem.348-349.181.

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Thermal barrier coating (TBC) is an essential requirement of a modern gas turbine engine. The TBC failure is the delamination and spallation. The oxidation damage under high temperature results in the reduction of interfacial adhesion. The interfacial fracture toughness is an important property to analyze the TBC failure. The interfacial fracture toughness of ceramic coating - bond coating has been researched in the past. However, the facture toughness of the bond coating - substrate due to the Al depletion was very few studied. In this study, a NiCrAlY bond coating by air plasma spray (APS) was deposited. The substrate was directionally solidified superalloy (DZ40M). Isothermal oxidation was performed at 10500 for 100h. Using the HXZ-1000 micro-hardness equipment, the five different times was chosen to test the hardness and the crack length, and then the fracture toughness was obtained. While the oxidation exposure time increased at 10500, the hardness of the substrate close to the bond coating decreased with the increase of the bond coating’ hardness. Meanwhile, the interfacial fracture toughness of the bond coating - substrate decreased because of the Al depletion.
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Pham, Hai Vu, and Makoto Nanko. "Crack-Healing Function of Nano-Ni/(ZrO2+Al2O3) Hybrid Materials." Materials Science Forum 804 (October 2014): 179–82. http://dx.doi.org/10.4028/www.scientific.net/msf.804.179.

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Ni/(ZrO2+Al2O3) nanocomposites have excellent mechanical properties, as well as self-healing function. The powder preparation was conducted by drying slurry consisting of distilled water, Al2O3, 3 mol % Y2O3doped ZrO2and nickel nitrate. After reduction at 600°C in a stream of Ar-1% H2, the powder mixture was consolidated by pulsed electric current sintering (PECS) at 1300°C for 5 min under 50 MPa. Surface cracks were generated by Vickers indentation on the polished surface of the test samples. Ni/(YZ+Al2O3) shows 1200 MPa in bending strength and 6.1 MPa m1/2in facture toughness. Crack-healing and oxidation tests were conducted at temperature ranging from 1100 to 1300°C in air. As a result, crack-disappearance occurred slightly faster than that of Ni/Al2O3.
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Pavelko, Vitalijs. "On the Crack Quasi-Static Growth." Key Engineering Materials 827 (December 2019): 312–17. http://dx.doi.org/10.4028/www.scientific.net/kem.827.312.

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The theoretical model of quasi-static crack growth in the elastic-plastic material under load variation in a wide range. Small-scale yielding is principal assumption and main restriction of proposed theory. The model of crack growth provides for continues and interrelated both the crack propagation and plastic deformation development. The nonlinear first-order differential equation describes the quasi-static process of crack growth. In dimensionless form this equation invariant in respect to geometrical configuration and material. The critical size of the plastic zone is proposed as the characteristics of material resistance which is directly connected with the fracture toughness, but more convenient in practical applications of invariant equation. The demonstration of solution is performed for the double cantilever beam that widely used as the standard (DCB) sample for measurement of the mode-I interlaminar fracture toughness. he short analysis of some properties of solution of the invariant equation and its application is done.
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Chasiotis, I., S. W. Cho, and K. Jonnalagadda. "Fracture Toughness and Subcritical Crack Growth in Polycrystalline Silicon." Journal of Applied Mechanics 73, no. 5 (December 10, 2005): 714–22. http://dx.doi.org/10.1115/1.2172268.

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The fracture behavior of polycrystalline silicon in the presence of atomically sharp cracks is important in the determination of the mechanical reliability of microelectromechanical system (MEMS) components. The mode-I critical stress intensity factor and crack tip displacements in the vicinity of atomically sharp edge cracks in polycrystalline silicon MEMS scale specimens were measured via an in situ atomic force microscopy/digital image correlation method. The effective (macroscopic) mode-I critical stress intensity factor for specimens from different fabrication runs was 1.00±0.1MPa√m, where 0.1MPa√m is the standard deviation that was attributed to local cleavage anisotropy and grain boundary effects. The experimental near crack tip displacements were in good agreement with the linearly elastic fracture mechanics solution, which supports K dominance in polysilicon at the scale of a few microns. The mechanical characterization method implemented in this work allowed for direct experimental evidence of incremental (subcritical) crack growth in polycrystalline silicon that occurred with crack increments of 1-2μm. The variation in experimental effective critical stress intensity factors and the incremental crack growth in brittle polysilicon were attributed to local cleavage anisotropy in individual silicon grains where the crack tip resided and whose fracture characteristics controlled the overall fracture process resulting in different local and macroscopic stress intensity factors.
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Zhang, M.-J., F.-X. Zhi, and X.-R. Su. "Fracture toughness and crack growth mechanism for multiphase polymers." Polymer Engineering and Science 29, no. 16 (August 1989): 1142–46. http://dx.doi.org/10.1002/pen.760291612.

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Sevillano, J. Gil. "Toughness and Fatigue Crack Growth Rate of Textured Metals." Textures and Microstructures 12, no. 1-3 (January 1, 1990): 77–87. http://dx.doi.org/10.1155/tsm.12.77.

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The influence of anisotropy of crystallographic origin on both fracture toughness and the rate of stage-II ductile fatigue crack growth in textured metals is discussed in terms of a plane-strain small geometry change solution for plastic non-hardening materials (a Prandtl-type slip-line field solution accounting for anisotropy). Results corresponding to FCC or BCC metals sliding, respectively, on {111} 〈110〉 or {110} 〈111〉 systems are presented. Remarkable effects of both texture toughening and fatigue crack growth rate anisotropy are predicted. Stronger effects are anticipated in more anisotropic metals (HCP).
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Dissertations / Theses on the topic "Facture toughness; Crack growth"

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Morsi, Khaled M. B. E. "Mechanical properties of particle reinforced alumina." Thesis, University of Oxford, 1995. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.320644.

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Lados, Diana Aida. "Fatigue crack growth mechanisms in Al-Si-Mg alloys." Link to electronic thesis, 2004. http://www.wpi.edu/Pubs/ETD/Available/etd-0204104-125758.

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Thesis (Ph. D.)--Worcester Polytechnic Institute.
Keywords: Microstructure; Elastic-Plastic Fracture Mechanics; Crack closure; A356; J-integral; Conventionally cast and SSM Al-Si-Mg alloys; Residual stress; Heat treatment; Fatigue crack growth mechanisms; Threshold stress intensity factor; Plastic zone; Paris law; Fracture toughness; Roughness. Includes bibliographical references.
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Shipsha, Andrey. "Failure of Sandwich Structures with Sub-Interface Damage." Doctoral thesis, Stockholm, 2001. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-3184.

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Herman, David M. "Fatigue crack growth and toughness of niobium silicide composities." online version, 2009. http://rave.ohiolink.edu/etdc/view.cgi?acc%5Fnum=case1228932584.

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Herman, David M. "Fatigue Crack Growth and Toughness of Niobium Silicide Composites." Case Western Reserve University School of Graduate Studies / OhioLINK, 2009. http://rave.ohiolink.edu/etdc/view?acc_num=case1228932584.

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Milan, Marcelo Tadeu. "Fatigue crack growth resistance and fracture toughness of selectively reinforced aluminium alloys." Thesis, University of Birmingham, 2002. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.251924.

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The main aim of this work was to investigate the fatigue crack growth resistance and fracture toughness of selectively reinforced Al alloys. In such bimaterials, the crack growth resistance is affected by the failure mechanism, the direction of crack approach to the interface and by the conflict between the elastic-plastic mismatch and residual stresses. When the crack approaches the interface from the composite side, in the A12124 based bimaterials, the fatigue crack growth rate is reduced below "composite only" values by the compressive residual stress, although the elastic-plastic mismatch was expected to cause the opposite effect. In the A16061 based bimaterials, although some crack deceleration is also observed, fatigue crack growth rates are above the "composite only" values presumably because these bimaterials have lower compressive residual stress and higher plastic mismatch near the interface. After crossing the interface, the crack driving force is affected by closure mechanisms developed on the composite side of the crack wake. Conversely, when the crack grows from the Al alloy side, for both A12124 and A16061 based bimaterials, the crack growth rate is mainly reduced by the elastic-plastic mismatch. After crossing the interface, the crack driving force is well described by the thermal residual stresses, unless a crack tip deflection reduces the Mode I near tip stresses. In a fracture toughness test, when the pre-crack tip is in the composite side of the A12124 based bimaterials, KQ(5%) values are increased above "composite only" values presumably due to the compressive residual stresses and despite the amplification of the crack driving force from the elastic-plastic mismatch. In the A16061 based bimaterials, due to the higher plastic mismatch and lower compressive residual stresses, KQ(5%) values are below "composite only" values. Additionally, for all bimaterials, KQ(5%) values increase if the pre-crack tip is closer to the interface. When the crack propagates, it extends to the interface, bifurcates and arrests. The load then had to be increased to promote the onset of plastic collapse. The crack tip blunting and deflection mechanism increases the toughness attained at the onset of plastic collapse of the bimaterials above "Al alloy only" values. Conversely, if the pre-crack tip is in the Al alloy side, the final failure is deduced to occur when damage accumulated on the composite side links to the pre-crack tip. When the pre-crack tip is at 2.0mm from the interface, for the A12124 based bimaterials, KQ(5%) values are in general lower than the "A12124 only" value due to the tensile residual stresses. For the A16061 based bimaterials, KQ(5%) values are as high as the "A16061 only" value presumably due to the higher plastic mismatch and lower tensile residual stress of such bimaterials. Additionally, for all bimaterials, KQ(5%) values increase if the precrack tip is at 0.5mm from the interface. If the pre-crack tip is at 2.0mm from the interface, Kerit and Scrit values of the bimaterial are higher than the "Al alloy only" value and this is deduced to be due to the increase in the elastic-plastic mismatch shielding and by delayed critical particle damage within the composite side. At 0.5mm from the interface, Keritt and Scrit values are reduced and this is deduced to be because both the near tip tensile residual stress is higher and critical particle damage occurs earlier on the composite side; moreover, the unreinforced Al alloy layer is thinner and the damage on the composite side is deduced to link more easily to the pre-crack tip. For a constant particle size, there is an optimum particle volume fraction in which both Kerit and Scrit values are maximised with respect to a specific pre-crack tip position.
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WATANABE, Katsuhiko, and Hideyuki AZEGAMI. "An Evaluation of the Fracture Resistance of a Stably Growing Crack by Crack Energy Density (1st Report, Derivation of Fundamental Relations and Proposal of Evaluation Method)." 日本機械学会, 1986. http://hdl.handle.net/2237/12159.

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Ingham, Edward John. "The development of impact toughness and resistance to slow crack growth in modified polyvinyl chloride and polyethylene pipe grade polymers." Thesis, Manchester Metropolitan University, 2003. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.271274.

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Lee, Ji Soo. "Time-Dependent Crack Growth in Brittle Rocks and Field Applications to Geologic Hazards." Diss., The University of Arizona, 2007. http://hdl.handle.net/10150/193784.

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The primary focus of this research is to evaluate the time-dependent crack growth in rocks using lab tests and numerical modeling and its application to geologic hazard problems. This research utilized Coconino sandstone and Columbia granite as the study materials and produced the subcritical crack growth parameters in both mode I and II loadings using the rock materials. The mode I loading test employs three different types of fracture mechanics tests: the Double Torsion (DT), the Wedge Splitting (WS), and the Double Cantilever Beam (DCB) test. Each test measured the mode I crack velocity. The DT test indirectly measured the crack velocity using the load relaxation method. The WS and DCB tests directly measured the crack velocity by monitoring using a video recording. The different mode I subcritical crack growth parameters obtained from the three tests are discussed. For the mode II loading test, this study developed a new shear fracture toughness test called the modified Punch-Through Shear (MPTS). The MPTS test conducted at different loading rates produced the mode II subcritical crack growth parameters. These fracture mechanics tests were calibrated and simulated using the distinct element method (DEM) and the finite element method (FEM). DEM analysis employed the particle flow code (PFC) to simulate the mixed mode crack growth and to match with the failure strength envelop of the triaxial compressive tests. FEM analysis employed the Phase2 program to analyze the crack tip stress distribution and the FRANC2D program to calculate the modes I and II stress intensity factors. The fracture mechanics tests and numerical modeling showed well the dependency of the mode II subcritical crack growth parameters according to confining pressure, loading rate, and the mode II fracture toughness. Finally, the UDEC modeling based on DEM is utilized in this study to forecast the long-term stability of the Coconino rock slope, as one of geologic hazards. The fracture mechanics approach is implemented in the program using the modes I and II subcritical crack growth parameters obtained from the lab tests and numerical modeling. Considering the progressive failure of rock bridges due to subcritical crack growth, the UDEC results predicted the stable condition of the Coconino rock cliff over 10,000 years. This result was validated by comparing it with the previous planar failure case.
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Yurtoglu, Mine Ender. "Mode Ii Fatigue Crack Growth Behavior And Mode Ii Fracture Toughness Of 7050 Aluminum Alloy In Two Orientations." Master's thesis, METU, 2013. http://etd.lib.metu.edu.tr/upload/12615581/index.pdf.

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Fatigue crack growth behavior of AA7050 T7451 aluminum alloy under mode II loading condition in two orientations was investigated. Compact shear specimens were prepared in TL and LT directions. A loading frame for mode II type of loading was manufactured. Using the loading frame and the specimen, KIIC values and mode II fatigue crack growth rates were calculated. Fractographic analysis of the fracture surfaces of both mode II fracture toughness test specimens and mode II fatigue crack growth test specimens were done to examine the effects of mode II load. KIIC values were measured between 1.3 and 1.5 times the KIC values for this alloy. As for mode II fatigue crack growth rates, TL orientation shows the highest mode II fatigue crack growth resistance.
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Books on the topic "Facture toughness; Crack growth"

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United States. National Aeronautics and Space Administration. Scientific and Technical Information Division., ed. Fracture toughness and crack growth of Zerodur. [Washington, DC]: National Aeronautics and Space Administration, Office of Management, Scientific and Technical Information Division, 1990.

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Fracture toughness and crack growth rates of irradiated austenitic stainless steels. Washington, D.C: Division of Engineering Technology, Office of Nuclear Regulatory Research, U.S. Nuclear Regulatory Commission, 2003.

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A compendium of sources of fracture toughness and fatigue crack growth data for metallic alloys. Hampton, Va: National Aeronautics and Space Administration, Langley Research Center, 1988.

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A compendium of sources of fracture toughness and fatigue crack growth data for metallic alloys. Hampton, Va: National Aeronautics and Space Administration, Langley Research Center, 1988.

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An evaluation of the fatigue crack growth and fracture toughness properties of beryllium-copper alloy CDA172. Houston, Tex: National Aeronautics and Space Administration, Lyndon B. Johnson Space Center, 1990.

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Ingham, Edward John. The development of impact toughness and resistance to slow crack growth in modified polyvinyl chloride and polyethylene pipe grade polymers. 2003.

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K, Chakrabarti Alok, Chesnutt J. C, and Metallurgical Society (U.S.), eds. Microstructure, fracture toughness, and fatigue crack growth rate in titanium alloys: Proceedings of the 1987 TMS-AIME annual symposia on effects of microstructure on fracture toughness and fatigue crack growth rate in titanium alloys, held at Marriott City Center, Denver, Colorado, 1987, February 24-25. Warrendale, Pa: Metallurgical Society, 1987.

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Book chapters on the topic "Facture toughness; Crack growth"

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Knott, John F. "Fracture Toughness and Hydrogen-Assisted Crack Growth in Engineering Alloys." In Hydrogen Effects in Materials, 385–408. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2013. http://dx.doi.org/10.1002/9781118803363.ch36.

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Hoffman, Mark, Jürgen Rödel, Martin Sternitzke, and Richard Brook. "Fracture Toughness and Subcritical Crack Growth in an Alumina/Silicon Carbide ‘Nanocomposite’." In Fracture Mechanics of Ceramics, 179–86. Boston, MA: Springer US, 1996. http://dx.doi.org/10.1007/978-1-4615-5853-8_14.

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Maugis, Daniel. "Sub-Critical Crack Growth, Surface Energy and Fracture Toughness of Brittle Materials." In Fracture Mechanics of Ceramics, 255–72. Boston, MA: Springer US, 1986. http://dx.doi.org/10.1007/978-1-4615-7026-4_20.

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Chen, Y., W. Y. Chen, B. Alexandreanu, K. Natesan, and A. S. Rao. "Crack Growth Rate and Fracture Toughness of CF3 Cast Stainless Steels at ~3 DPA." In The Minerals, Metals & Materials Series, 673–87. Cham: Springer International Publishing, 2017. http://dx.doi.org/10.1007/978-3-319-68454-3_52.

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Chen, Y., W. Y. Chen, B. Alexandreanu, K. Natesan, and A. S. Rao. "Crack Growth Rate and Fracture Toughness of CF3 Cast Stainless Steels at ~3 DPA." In The Minerals, Metals & Materials Series, 1889–903. Cham: Springer International Publishing, 2017. http://dx.doi.org/10.1007/978-3-030-04639-2_128.

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Logsdon, W. A. "Tensile, Fracture Toughness and Fatigue Crack Growth Rate Properties of HP 9–4–30." In Advances in Cryogenic Engineering Materials, 355–60. Boston, MA: Springer US, 1986. http://dx.doi.org/10.1007/978-1-4613-9871-4_42.

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Wallace, A. C. "The Development of Curved Fracture Toughness Specimens for Predicting Crack Growth in Candu Reactor Pressure Tubes." In Time-Dependent Fracture, 281–91. Dordrecht: Springer Netherlands, 1985. http://dx.doi.org/10.1007/978-94-009-5085-6_24.

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Miyahara, Nobuyuki, Yoshiharu Mutoh, Kouhei Yamaishi, Keizo Uematsu, and Makoto Inoue. "The Effects of Grain Size on Strength, Fracture Toughness, and Static Fatigue Crack Growth in Alumina." In Grain Boundary Controlled Properties of Fine Ceramics, 125–36. Dordrecht: Springer Netherlands, 1992. http://dx.doi.org/10.1007/978-94-011-1878-1_14.

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Yoda, M., N. Ogawa, and K. Ono. "Effects of Residual Stress on Fracture Toughness and Subcritical Crack Growth of Indented Cracks in Various Glasses." In Fracture Mechanics of Ceramics, 161–66. Boston, MA: Springer US, 1996. http://dx.doi.org/10.1007/978-1-4615-5853-8_12.

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Radovic, M., E. Lara-Curzio, and G. Nelson. "Fracture Toughness and Slow Crack Growth Behavior of Ni-YSZ and YSZ as a Function of Porosity and Temperature." In Advances in Solid Oxide Fuel Cells II: Ceramic Engineering and Science Proceedings, Volume 27, Issue 4, 373–81. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2008. http://dx.doi.org/10.1002/9780470291337.ch36.

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Conference papers on the topic "Facture toughness; Crack growth"

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Stan, Felicia. "Study of the Dynamic Crack Growth of a Planar Crack Front in Three-Dimensional Body Subjected to Mode I Loading." In ASME 2008 International Manufacturing Science and Engineering Conference collocated with the 3rd JSME/ASME International Conference on Materials and Processing. ASMEDC, 2008. http://dx.doi.org/10.1115/msec_icmp2008-72239.

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In this paper, a methodology is presented for predicting crack growth rate along three-dimensional crack fronts under mode I dynamic loading conditions. Within the present methodology, for every point along the crack front the stress intensity factor matches the dynamic fracture toughness at the onset of propagation. In order to accurately evaluate the dynamic stress intensity factor the component separation method of the dynamic J integral is used. To overcome the difficulties in three-dimensional dynamic fracture simulations, the three-dimensional dynamic moving finite element method based on three-dimensional moving 20-noded isoparametric elements is used. In the absence of experimental measurements for dynamic fracture toughness, a new methodology to estimate the dynamic fracture toughness is proposed, i.e., a hybrid experimental-numerical approach, which makes use of numerically determined histories of the dynamic stress intensity factor. The values of the dynamic stress intensity factor are converted into dynamic fracture toughness based on the Weibull distribution. The predictive ability of the developed methodology is demonstrated through the prediction of the dynamic crack growth in Double Cantilever Beam (DCB) specimen of PMMA with different thickness.
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Tognarelli, Michael A., Ramgopal Thodla, and Steven Shademan. "Fatigue Crack Growth Rate and Fracture Toughness of API5L X65 in Sweet Environments." In ASME 2013 32nd International Conference on Ocean, Offshore and Arctic Engineering. American Society of Mechanical Engineers, 2013. http://dx.doi.org/10.1115/omae2013-10216.

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Corrosion fatigue and fracture toughness in sour environments of APIX65 5L have typically been studied in relatively severe environments like NACE A and NACE B solutions. There are very limited data in sweet and mildly sour environments that are of interest in various applications. This paper presents fatigue crack growth frequency scans in a range of sweet and mildly sour environments as well as on different microstructures: Parent Pipe, Heat Affected Zone (HAZ) and Weld Center Line (WCL). The fatigue crack growth rate (FCGR) increased with decreasing frequency and reached a plateau value at low frequencies. FCGR in the sweet environments that were investigated did exhibit a frequency dependence (increasing with decreasing frequency) and had plateau FCGR in the range of 10–20× the in-air values. In the mildly sour environments that were investigated, FCGR was found to be about 25 to 30× higher than the in-air values. By comparison, in NACE A environments the FCGR is typically about 50× higher than the in-air values. The FCGRs of parent pipe and HAZ were found to be similar over a range of environments, whereas the WCL FCGR data were consistently lower by about a factor of 2×. The lower FCGR of the WCL is likely due to the lower concentration of diffusible hydrogen in the weld. FCGRs as a function of ΔK (stress integrity factor range) were measured on parent pipe at the plateau frequency. The measured Paris law curves were consistent with the frequency scan data. Rising displacement fracture toughness tests were performed in a range of sweet and sour environments to determine the R-curve behavior. Tests were performed in-situ at a slow K-rate of 0.05Nmm−3/2/s over a range of environmental conditions on parent pipe. The initiation toughness and the slope of the R-curve decreased sharply in the sour environments. The initiation toughness and slopes were largely independent of the notch location as well as environmental conditions. Typical values of initiation toughness were in the range of 90–110N/mm.
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Xu, S., R. Bouchard, and W. R. Tyson. "Flow Behaviour and Ductile Fracture Toughness of a High Toughness Steel." In 2004 International Pipeline Conference. ASMEDC, 2004. http://dx.doi.org/10.1115/ipc2004-0192.

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This paper reports results of tests on flow and ductile fracture of a very high toughness steel with Charpy V-notch absorbed energy (CVN energy) at room temperature of 471 J. The microstructure of the steel is bainite/ferrite and its strength is equivalent to X80 grade. The flow stress was determined using tensile tests at temperatures between 150°C and −147°C and strain rates of 0.00075, 0.02 and 1 s−1, and was fitted to a proposed constitutive equation. Charpy tests were carried out at an initial impact velocity of 5.1 ms−1 using drop-weight machines (maximum capacity of 842 J and 4029 J). The samples were not broken during the test, i.e. they passed through the anvils after significant bending deformation with only limited crack growth. Most of the absorbed energy was due to deformation. There was little effect of excess energy on absorbed energy up to 80% of machine capacity (i.e. the validity limit of ASTM E 23). As an alternative to the CVN energy, the crack tip opening angle (CTOA) measured using the drop-weight tear test (DWTT) has been proposed as a material parameter to characterize crack propagation resistance. Preliminary work on evaluating CTOA using the two-specimen CTOA test method is presented. The initiation energy is eliminated by using statically precracked test specimens. Account is taken of the geometry change of the specimens (e.g. thickening under the hammer) on the rotation factor and of the effect of strain rate on flow stress.
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Wang, Z. X., Y. J. Chao, and P. S. Lam. "Crack Growth in 18G2A Steels With Different Constraint." In ASME 2007 Pressure Vessels and Piping Conference. ASMEDC, 2007. http://dx.doi.org/10.1115/pvp2007-26435.

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A constraint theory in fracture mechanics is used to analyze the test data of 18G2A steels using single edge-notched bend (SENB) specimens with various crack depth to specimen width ratios (a/W). A bending correction factor is included in the two-parameter (J-A2) asymptotic solution to improve the theoretical prediction of the stress field for deep cracks under large scale yielding condition, where J is the J-integral and A2 is the constraint parameter, which depends on the in-plane geometry of the cracked body (a/W). As a result, the valid region for a traditional J-controlled crack growth is extended, and the ASTM specimen size requirements for fracture toughness testing can be relaxed. In addition, it is shown that the functional dependence of J-R curves on A2 for 18G2A steels is established with test data; and the predicted J-R curves agree very well with the experimental curves. This ensures the transferability of laboratory test data to an actual structure provided the constraint level (A2) of the cracked structure is known or determined. This allows an appropriate J-R curve with the same constraint level to be constructed and used in flaw stability analysis of any cracked body.
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Kalyanam, S., G. M. Wilkowski, D. J. Shim, F. W. Brust, Y. Hioe, G. Wall, and P. Mincer. "Why Conduct SEN(T) Tests and Considerations in Conducting/Analyzing SEN(T) Testing." In 2010 8th International Pipeline Conference. ASMEDC, 2010. http://dx.doi.org/10.1115/ipc2010-31631.

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This paper outlines a methodology used to conduct a SEN(T) fracture test and discusses the analysis procedure used to obtain J-R and CTOD-R resistance curves from the experimental data. The CTOD-R curve depicts the change in toughness with crack growth, in a manner similar to the J-R curve methodology. Significant crack growth can arise from the start of ductile tearing to maximum load in the case of surface-cracked pipes with heavier-wall piping used in recent designs of natural gas pipelines that are required to handle greater pressures and much lower temperatures. CTOD-R curves provide toughness values that are a factor of 2 to 3 times higher at maximum load when compared to the toughness at crack initiation. The impacts of this on stress and strain-based design of pipelines are highlighted. Further, the differences between the traditional approach that uses the crack-tip-opening-displacement at the initial crack tip (CTOD′) versus the more recent developments that employ the crack-tip-opening-displacement at the growing crack tip (CTOD) are examined. The CTOD-R curve for the growing crack tip is more consistent with J-R curve analyses. Single-edge-notched bend [SEN(B)] or popularly called bend-bar specimens are used for crack-tip-opening-displacement (CTOD) as well as J-integral toughness testing. This paper discusses the advantages of using the fracture toughness data determined from a single-edge-notched tension [SEN(T)] specimen from considerations of the constraints faced by surface cracks in pipelines and the differences in fracture toughness values seen between the SEN(T) and SEN(B) specimens in the transition temperature region.
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Ferreira, Claudinei, Diego F. S. Burgos, and Claudio Ruggieri. "Fracture Toughness Testing of an Overmatched Pipe Girth Weld Using Clamped SE(T) Specimens." In ASME 2019 Pressure Vessels & Piping Conference. American Society of Mechanical Engineers, 2019. http://dx.doi.org/10.1115/pvp2019-93256.

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Abstract This work presents an investigation of the ductile tearing properties for a girth weld made of an ASTM A106 Gr C steel using the SMAW welding process with a low hydrogen E7018 electrode thereby resulting in a weld with high strength overmatching with respect to the base material. Testing of the pipe girth welds employed side-grooved, clamped SE(T) specimens with a weld centerline notch to determine the crack growth resistance curves based upon the unloading compliance (UC) method using a single specimen technique. Recently developed compliance functions and η-factors applicable to weld centerline notched SE(T) specimens are introduced to determine crack growth resistance data from laboratory measurements of load-displacement records. While the UC procedure resulted in measured crack extensions for the tested specimens with weld centerline notch that underestimated the 9-point average crack extension, our preliminary results demonstrate the capability of the methodology in describing crack growth resistance behavior which serves as a basis for ductile tearing assessments in ECA procedures applicable to overmatched girth welds and similar structural components.
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Song, Eun Ju, and Joseph A. Ronevich. "Orientation Dependence of Hydrogen Accelerated Fatigue Crack Growth Rates in Pipeline Steels." In ASME 2018 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2018. http://dx.doi.org/10.1115/pvp2018-84835.

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One of the most efficient methods for supplying gaseous hydrogen long distances is by using steel pipelines. However, steel pipelines exhibit accelerated fatigue crack growth rates in gaseous hydrogen relative to air. Despite conventional expectations that higher strength steels would be more susceptible to hydrogen embrittlement, recent testing on a variety of pipeline steel grades has shown a notable independence between strength and hydrogen assisted fatigue crack growth rate. It is thought that microstructure may play a more defining role than strength in determining the hydrogen susceptibility. Among the many factors that could affect hydrogen accelerated fatigue crack growth rates, this study was conducted with an emphasis on orientation dependence. The orientation dependence of toughness in hot rolled steels is a well-researched area; however, few studies have been conducted to reveal the relationship between fatigue crack growth rate in hydrogen and orientation. In this work, fatigue crack growth rates were measured in hydrogen for high strength steel pipeline with different orientations. A significant reduction in fatigue crack growth rates were measured when cracks propagated perpendicular to the rolling direction. A detailed microstructural investigation was performed, in an effort to understand the orientation dependence of fatigue crack growth rate performance of pipeline steels in hydrogen environments.
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Szwedowicz, Jaroslaw, Piotr Bednarz, Christoph Meilgen, and Jeff Samuelson. "Crack Growth Under Cyclic Loading and Plasticity Conditions." In ASME Turbo Expo 2014: Turbine Technical Conference and Exposition. American Society of Mechanical Engineers, 2014. http://dx.doi.org/10.1115/gt2014-25450.

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The increasing use of renewable energy sources to produce electricity requires additional operational flexibility from fossil-fuel gas and steam turbines. To compensate for renewable energy fluctuations in the electrical grid, a gas turbine (GT) engine needs to be more flexible, operating in peaking and partial loading modes as well as the base-load operation mode. Understanding how these different modes affect the lifetime of turbine components is critical to ensuring favourable RAM (Reliability, Availability, and Maintainability). Component lifetimes in peaking modes are limited by the number of thermo-mechanical cycles that a component can experience before crack initiation. The useful lifetime of some components can be increased by basing the predicted lifetime on the number of cycles for crack initiation plus the number of cycles for the crack to reach its maximum allowable length based on the fracture toughness K1C criterion for linear elastic fracture mechanics (LEFM). This is usually accomplished by using the Paris law to predict the rate of crack growth. Once cracks are formed, further propagation depends on the states of stress and strain near the cracks. These factors, which drive crack growth, can be quantified by the energy release rate. The Paris law predicts crack growth as a function of the energy release rate under linear elastic conditions, commonly for load controlled tests with load ration R>0. However, large thermal and mechanical loading can result in plastic deformation under cyclic loading conditions. Most GT components operate under strain controlled conditions generated by thermal loading. In this paper, a novel method is used to characterize crack growth under cyclic strain conditions in regions under plastic strain. The experimental data reveal that the rate of crack growth changes under plastic conditions in comparison with the linear elastic case. Especially compared to very high stress intensities ΔK of load controlled tests, here the allowable displacement limiting strain control matters. Applying experimental data from material tested under cyclic loading and elastic-plastic material response, component lifetime has been reliably predicted. Hereafter the developed method is referred to as elastic plastic fracture mechanics (EPFM) lifetime assessment. The EPFM approach more closely predicts the observed rate of crack growth than linear elastic fracture mechanics. LEFM over-predicts component lifetime for cracks growing in plastic regions under cyclic loading and could lead to catastrophic failure of a component. Therefore, the lifetime of a highly loaded component is more reliably assessed using the EPFM approach, as demonstrated for two alloys in this paper.
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Williams, Bruce W., William R. Tyson, C. Hari M. Simha, and Bogdan Wasiluk. "Specimen Curvature and Size Effects on Crack Growth Resistance From Compact Tension Specimens of CANDU Pressure Tubes." In ASME 2019 Pressure Vessels & Piping Conference. American Society of Mechanical Engineers, 2019. http://dx.doi.org/10.1115/pvp2019-93318.

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Abstract CSA Standard N285.8 requires leak-before-break and fracture protection for Zr-2.5Nb pressure tubes in operating CANDU reactors. In-service deuterium uptake causes the formation of hydrides, which can result in additional variability and reduction of fracture toughness. Pressure tube fracture toughness is assessed mainly through rising pressure tube section burst tests. Given the length of the ex-service pressure tubes required for burst testing and the requirement to increase the hydrogen content of irradiated ex-service pressure tubes, only a limited number of burst tests can be performed. Using small-scale compact tension, C(T), specimens are advantageous for obtaining a statistically significant number of fracture toughness measurements while using less ex-service pressure tube material. This work focuses on the study of C(T) geometry designs in order to obtain crack growth resistance and fracture toughness closer to those deduced from burst tests. Because C(T) specimens must be machined from pressure tubes of about 100 mm in diameter and 4 mm in wall thickness, they are out-of-plane curved. As well, they undergo significant tunnelling during crack extension. These two factors can result in a violation of the ASTM standard for fracture toughness testing. The current work examined the influence of specimen curvature and tunnelled crack front on the crack growth resistance curve, or J-R curve. Finite element (FE) models using stationary and growing cracks were used in a detailed numerical investigation. To capture crack tunnelling in the FE models, a damage mechanics approach was adopted, with the critical strain to accumulate damage being a function of crack front stress triaxiality. The J-integral numerically estimated from the domain integral approach was compared to the J-integral calculated from the analytical equations in the ASTM E-1820 standard. In most cases, the difference between the numerical and the standard estimations was less than 10%, which was considered acceptable. It was found that at higher load levels of load-line-displacement, specimen curvature influenced the J-integral results. Crack tunnelling was shown to have a small influence on the estimated J-integrals, in comparison with the straight crack fronts. A modest number of experiments were carried out on unirradiated Zr-2.5Nb pressure tube material using three designs of curved C(T) specimens. It was found that the specimens of both designs that featured a width of 34 mm had more than twice the crack extension of the specimens of the 17-mm width design. The 17-mm width specimens are used mainly to assess the small-scale fracture toughness of pressure tube material. Additionally, the applied J-integral at the maximum load was about 1.4 times higher for the larger-width C(T) specimens. These C(T) specimens also produced J-R curves with greater crack extensions, which were closer to those obtained from the pressure tube section burst tests. Artificially hydrided pressure tube material was not considered in the current work, to avoid any potential source of experimental variability; however, it should be considered in future work.
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Onizawa, Kunio, Katsuyuki Shibata, Masahide Suzuki, Daisuke Kato, and Yinsheng Li. "Embedded Crack Treatments and Fracture Toughness Evaluation Methods in Probabilistic Fracture Mechanics Analysis Code for the PTS Analysis of RPV." In ASME/JSME 2004 Pressure Vessels and Piping Conference. ASMEDC, 2004. http://dx.doi.org/10.1115/pvp2004-2720.

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Using the probabilistic fracture mechanics analysis code PASCAL, we studied the treatment method of an embedded crack and the fracture toughness evaluation methods on the probability of crack initiation and fracture of a reactor pressure vessel (RPV). For calculating the stress intensity factor (SIF) of an embedded crack, the ASME and CRIEPI procedures were introduced into the PASCAL code. The CRIEPI method enables us to calculate the SIF values at three points on the crack tip. Under a severe pressurized thermal shock (PTS) condition, the crack growth analysis methods with different SIF calculation points and crack growth directions are compared. To evaluate precisely the fracture toughness after neutron irradiation, the new fracture toughness curves based on the Weibull distribution were incorporated into the PASCAL code. The calculated results with these new curves showed little difference in the conditional probabilities of RPV fracture as compared to the curve currently used in the U.S.
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Reports on the topic "Facture toughness; Crack growth"

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Chopra, O. K., E. E. Gruber, and W. J. Shack. Fracture toughness and crack growth rates of irradiated austenitic stainless steels. Office of Scientific and Technical Information (OSTI), June 2003. http://dx.doi.org/10.2172/822551.

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Alexander, D. J., and B. G. Gieseke. Fracture toughness and fatigue crack growth of oxide dispersion strengthened copper. Office of Scientific and Technical Information (OSTI), April 1996. http://dx.doi.org/10.2172/270445.

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Chen, Y., B. Alexandreanu, and K. Natesan. Crack Growth Rate and Fracture Toughness Tests on Irradiated Cast Stainless Steels. Office of Scientific and Technical Information (OSTI), June 2013. http://dx.doi.org/10.2172/1084189.

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Davidson, D. L. Micromechanisms of Fatigue Crack Growth and Fracture Toughness in Metal Matrix Composites. Fort Belvoir, VA: Defense Technical Information Center, April 1993. http://dx.doi.org/10.21236/ada265153.

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Chopra, O. K., and W. J. Shack. Crack growth rates and fracture toughness of irradiated austenitic stainless steels in BWR environments. Office of Scientific and Technical Information (OSTI), January 2008. http://dx.doi.org/10.2172/932944.

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Gilman, J. BWRVIP-140NP: BWR Vessel and Internals Project Fracture Toughness and Crack Growth Program on Irradiated Austenitic Stainless Steel. Office of Scientific and Technical Information (OSTI), March 2005. http://dx.doi.org/10.2172/839513.

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Chopra, Omesh K. Effects of Thermal Aging and Neutron Irradiation on Crack Growth Rate and Fracture Toughness of Cast Stainless Steels and Austenitic Stainless Steel Welds. Office of Scientific and Technical Information (OSTI), October 2014. http://dx.doi.org/10.2172/1178101.

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