R-curve modeling for Ni/Al2O3 laminates

Mekky, Waleed; Nicholson, Patrick S.

doi:10.1016/j.compositesb.2006.05.001

Cited by 8 publications

(5 citation statements)

References 46 publications

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“…Equating the load-line displacement to the bridging law given by Eq. (9), which represents the materials resistance to crack opening in the bridging zone, leads one to (15) in which the function f are functions of the crack geometry. Four different crack geometries including double cantilever beam, single cantilever bend, single-edge bend (SEB), and T-crack geometries were included in the micromechanical code.…”

Section: Micromechanical Code For Structural Analysismentioning

confidence: 99%

“…The weight function for SEB was taken from the paper by Fett and Munez [13], while the weight function for the T-crack was treated as a SCB crack with a fixed end [14]. The integral equation was solved by utilizing the polynomial expansion approach described by Mekky and Nicholson [15] and by Fett et al [16].…”

Section: Micromechanical Code For Structural Analysismentioning

confidence: 99%

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Model for the Effect of Fiber Bridging on the Fracture Resistance of Reinforced-Carbon-Carbon

Chan

Lee

Hudak

2011

Journal of Engineering Materials and Technology

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A micromechanical methodology has been developed for analyzing fiber bridging and resistance-curve behavior in reinforced-carbon-carbon (RCC) panels with a 3D composite architecture and a SiC surface coating. The methodology involves treating fiber bridging traction on the crack surfaces in terms of a weight function approach and a bridging law that relates the bridging stress to the crack opening displacement. A procedure has been developed to deduce material constants in the bridging law from the linear portion of the K-resistance curve. This approach has been applied to analyzing R-curves of RCC generated using double cantilever beam and single cantilever bend specimens to establish a bridging law for RCC. The bridging law has been implemented into a micromechanical code for computing the fracture response of a bridged crack in a structural analysis. The crack geometries considered in the structural analysis include the penetration of a craze crack in SiC into the RCC as a single-edge crack under bending and the deflection of a craze crack in SiC along the SiC/RCC interface as a T-shaped crack under bending. The proposed methodology has been validated by comparing the computed R-curves against experimental measurements. The analyses revealed substantial variations in the bridging stress (σo ranges from 11 kPa to 986 kPa, where σo is the limiting bridging stress) and the R-curve response for RCC due to the varying number of bridging ligaments in individual specimens. Furthermore, the R-curve response is predicted to depend on crack geometry. Thus, the initiation toughness at the onset of crack growth is recommended as a conservative estimate of the fracture resistance in RCC. If this bounding structural integrity analysis gives unacceptably conservative predictions, it would be possible to employ the current fiber bridging model to take credit for extra fracture resistance in the RCC. However, due to the large scatter of the inferred bridging stress in RCC, such an implementation would need to be probabilistically based.

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Section: Micromechanical Code For Structural Analysismentioning

confidence: 99%

Section: Micromechanical Code For Structural Analysismentioning

confidence: 99%

Model for the Effect of Fiber Bridging on the Fracture Resistance of Reinforced-Carbon-Carbon

Chan

Lee

Hudak

2011

Journal of Engineering Materials and Technology

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“…Several ceramic composites and, in particular, laminated structures were developed in recent years to enhance strength, toughness and to improve flaw tolerance. Fracture resistance and R-curve behaviour were achieved in laminated composites with (i) thin layers in residual compression alternated to thick layers in tension able to arrest surface and internal cracks and produce a threshold strength (Rao et al, 1999;Orlovskaya et al, 2005;Bermejo et al, 2006;Bermejo & Danzer, 2010;Nahliḱ et al, 2010), (ii) weak or porous interlayers that generate graceful and tortuous crack propagation paths (Davis et al, 2000;She et al, 2000), (iii) high strength surface layers and high toughness core, able to arrest starting surface flaws and to limit long cracks propagation, respectively, (Cho et al, 2001) and (iv) metallic layers that promote ductile bridging effects (Mekky & Nicholson, 2007). The limitations of such laminates are related to processing difficulties and to the fact that they can be used only when the tensile load is applied parallel to the layers, thus being not easily suitable to produce real components such as shells or tubes.…”

Section: Introductionmentioning

confidence: 99%

High Reliability Alumina-Silicon Carbide Laminated Composites by Spark Plasma Sintering

Sglavo¹,

Genua²

2011

Properties and Applications of Silicon Carbide

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“…S everal laminate structures were studied in recent years as possible solutions to overcome the traditional brittleness and low reliability of ceramic materials. Laminates with (i) metallic layers that promote ductile bridging effects, 1 with weak or porous interlayers that introduce low‐energy paths for crack propagation, 2,3 (ii) high strength surface layers and a high toughness body in order to combine and optimize both the characteristics, 4 and (iii) thin layers in residual compression alternating with thick layers in tension in order to arrest cracks and produce a threshold strength 5 have been proposed. The limitations of such laminates rely on processing difficulties and the fact that they can be used only with a specific orientation with respect to the applied load, and therefore they are not easily suitable to produce real components such as shells or tubes.…”

Section: Introductionmentioning

confidence: 99%

Alumina/Silicon Carbide Laminated Composites by Spark Plasma Sintering

Genua

Molinari

Casari³

2009

Journal of the American Ceramic Society

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Ceramic laminates composed of alumina/silicon carbide composite layers were produced by spark plasma sintering (SPS). Monolithic composite disks containing up to 30 vol% of silicon carbide were fabricated by stacking together and cosintering by SPS green layers prepared by tape casting water‐based suspensions. An engineered laminate with a specific layer combination that is able to promote the stable growth of surface defects before final failure was also designed and produced. Fully dense materials with an optimum adhesion between the constituting layers and a homogeneous distribution of the two phases were obtained after SPS. Monolithic composites showed an increasing strength with SiC load, and biaxial strength values as high as 700 MPa were observed for a SiC content of 30 vol%. The engineered laminate showed a peculiar crack propagation that is responsible for the high strength value of about 600 MPa and for the evident insensitivity to surface defects.

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R-curve modeling for Ni/Al2O3 laminates

Cited by 8 publications

References 46 publications

Model for the Effect of Fiber Bridging on the Fracture Resistance of Reinforced-Carbon-Carbon

Model for the Effect of Fiber Bridging on the Fracture Resistance of Reinforced-Carbon-Carbon

High Reliability Alumina-Silicon Carbide Laminated Composites by Spark Plasma Sintering

Alumina/Silicon Carbide Laminated Composites by Spark Plasma Sintering

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