Slip Systems and Their Critical Shear Stress in 3% Silicon Iron

Taoka, Tadami; Takeuchi, Shin; Furubayashi, Ei-ichi

doi:10.1143/jpsj.19.701

Cited by 138 publications

(21 citation statements)

References 8 publications

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“…Fatigue fracture toughness (K fc ) was calculated to be 7 MPam 1/2 from the maximum cyclic load during introducing the fatigue crack. This slip system was identical with the primary slip system of this bulk material [9,10]. Figure 5 shows load-displacement curves during fracture testing of micro-sized specimens.…”

Section: Fracture Behavior Of Millimeter-sized Specimenmentioning

confidence: 98%

Effects of Sample Size on the Fracture Behavior in Fe-3%Si Alloy Single Crystals

et al. 2006

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Fracture tests have been performed for both macro-and micro-sized specimens prepared from an Fe-3%Si alloy single crystal, and the effects of specimen size on fracture behavior have been investigated. Micro-sized cantilever beam specimens with dimensions of 10 x 10 x 50 µm 3 were prepared by focused ion beam machining. Notches with a depth of 5 µm were introduced into the micro-sized specimens and fatigue pre-crack was also introduced ahead of the notch. Macro-sized three-point bending specimens with dimensions of 2 x 2 x 10 mm 3 were also cut from the same Fe-3%Si alloy single crystal. Notches with a depth of 1mm were introduced into the macro-sized specimens, and fatigue pre-crack was also introduced. The notch plane was set to be (100), which is a cleavage plane of this material, and the notch direction was set to be [010] for both size of specimens. For macro-sized specimens, cleavage fracture occurred during introducing fatigue pre-crack. In contrast, the micro-sized specimens were fractured by ductile manner. A plastic zone was clearly observed on the specimen surface near the crack tip and dimples were found on the fracture surface. The plastic zone size of this material is calculated to be 90 µm. This size is small enough to satisfy small scale yielding for macro-sized specimens, although this size corresponds to large scale yielding in micro-sized specimens. This may cause the size effect on the fracture behavior of this material.

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Section: Fracture Behavior Of Millimeter-sized Specimenmentioning

confidence: 98%

Effects of Sample Size on the Fracture Behavior in Fe-3%Si Alloy Single Crystals

et al. 2006

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“…No possibility were found when this work was done to adjust those parameters on sub-scale simulations in ferrite. Thus, it was chosen to rely on usual knowledge about hardening mechanisms in ferrite [40,41]. Two gliding system families were considered: h1 1 1i{1 1 0} and h1 1 1i{1 1 2}, they will be named respectively F 110 and F 112 in the following.…”

Section: Ferrite and Carbide Clusters Behavioursmentioning

confidence: 99%

A micromechanical interpretation of the temperature dependence of Beremin model parameters for french RPV steel

Mathieu

Inal

Berveiller

et al. 2010

Journal of Nuclear Materials

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International audienceLocal approach to brittle fracture for low-alloyed steels is discussed in this paper. A bibliographical introduction intends to highlight general trends and consensual points of the topic and evokes debatable aspects. French RPV steel 16MND5 (equ. ASTM A508 Cl.3), is then used as a model material to study the influence of temperature on brittle fracture. A micromechanical modelling of brittle fracture at the elementary volume scale already used in previous work is then recalled. It involves a multiscale modelling of microstructural plasticity which has been tuned on experimental inter-phase and inter-granular stresses heterogeneities measurements. Fracture probability of the elementary volume can then be computed using a randomly attributed defect size distribution based on realistic carbides repartition. This defect distribution is then deterministically correlated to stress heterogeneities simulated within the microstructure using a weakest-link hypothesis on the elementary volume, which results in a deterministic stress to fracture. Repeating the process allows to compute Weibull parameters on the elementary volume. This tool is then used to investigate the physical mechanisms that could explain the already experimentally observed temperature dependence of Beremin's parameter for 16MND5 steel. It is showed that, assuming that the hypothesis made in this work about cleavage micro-mechanisms are correct, effective equivalent surface energy (i.e. surface energy plus plastically dissipated energy when blunting the crack tip) for propagating a crack has to be temperature dependent to explain Beremin's parameters temperature evolution

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“…Moreover experimental observations are generally classified into two categories. The first type is that slip occurs in the h111i direction on {110}, {211} and sometimes {321} planes, [1][2][3][4] and the second one is that slip occurs in the h111i direction on maximum resolved shear stress planes or noncrystallographic planes. [5][6][7][8] A common interpretation of these experimental observations described in the literatures on the theory of dislocations or the plastic deformation is as follows.…”

Section: Introductionmentioning

confidence: 99%

Possible Slip Systems in Body Centered Cubic Iron

Watanabe

2006

Mater. Trans.

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The slip systems along the h111i direction in bcc iron are investigated by the energy of the generalized stacking fault, or of the stacking fault between two adjacent crystallographic planes of perfect crystals, in order to obtain the knowledge of the slip phenomena in bcc single crystals. For systematic study, the 15 kinds of slip systems along the h111i direction from f110gh111i up to f954gh111i, f972gh111i and f981gh111i slip systems are taken into account. The energy of the stacking fault is evaluated by the molecular mechanics method with the embedded atom potential of Finnis-Sinclair type as a function of relative displacement of one side of the two half-crystals across the fault plane in the h111i direction. The maximum values of the fault energies for the slip systems whose slip planes have angles of less than approximately 15 degrees to the {110} plane are nearly same as that for the most preferable f110gh111i slip system. The maximum value for the f321gh111i slip system is the greatest among the currently analyzed 15 slip systems. The maximum value for the f211gh111i slip system is in the middle of those for the f110gh111i and f321gh111i slip systems, and those for the slip systems whose slip planes have angles between approximately 20 degrees and 30 degrees to the {110} plane are close to that for the f211gh111i slip system. In general, there is not inverse correlation between the maximum value of the fault energies for the slip system and the interplanar spacing of the considered slip system, although there is inverse correlation between them within the three slip systems which have three lowest index planes, namely, the f110gh111i, f211gh111i and f321gh111i slip systems.

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Slip Systems and Their Critical Shear Stress in 3% Silicon Iron

Cited by 138 publications

References 8 publications

Effects of Sample Size on the Fracture Behavior in Fe-3%Si Alloy Single Crystals

Effects of Sample Size on the Fracture Behavior in Fe-3%Si Alloy Single Crystals

A micromechanical interpretation of the temperature dependence of Beremin model parameters for french RPV steel

Possible Slip Systems in Body Centered Cubic Iron

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