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Journal articles on the topic 'Persistent slip band'

Author: Grafiati

Published: 4 June 2021

Last updated: 2 February 2022

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1

Sauzay, Maxime, Pierre Evrard, and Karine Bavard. "Influence of Slip Localization on Surface Relief Formation and Grain Boundary Microcrack Nucleation." Key Engineering Materials 465 (January 2011): 35–40. http://dx.doi.org/10.4028/www.scientific.net/kem.465.35.

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Slip localization is often observed in metallic polycrystals after cyclic deformation (persistent slip bands) or pre-irradiation followed by tensile deformation (channels). To evaluate its influence on surface relief formation and grain boundary microcrack nucleation, crystalline finite element (FE) computations are carried out using microstructure inputs (slip band aspect ratio/spacing). Slip bands (low critical resolved shear stress (CRSS)) are embedded in small elastic aggregates. Slip band aspect ratio and neighboring grain orientations influence strongly the surface slips. But only a weak effect of slip band CRSS, spacing and grain boundary orientation is observed. Analytical formulae are deduced which allow an easy prediction of the surface and bulk slips. The computed slips are in agreement with experimental measures (AFM/TEM measures on pre-irradiated austenitic stainless steels and nickel, copper and precipitate-strengthened alloy subjected to cyclic loading). Grain boundary normal stresses are computed for various materials and loading conditions. A square root dependence with respect to the distance to the slip band corner is found similarly to the pile-up stress field. But the equivalent stress intensity factor is considerably lower. Analytical formulae are proposed for predicting the grain boundary normal stress field depending on the microstructure lengths. Finally, an energy balance criterion is applied using the equivalent elastic energy release rate and the surface/grain boundary energies. The predicted macroscopic stresses for microcrack nucleation are compared to the experimental ones.

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2

Schiller, C., and D. Walgraef. "Numerical simulation of persistent slip band formation." Acta Metallurgica 36, no. 3 (1988): 563–74. http://dx.doi.org/10.1016/0001-6160(88)90089-2.

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3

Kolář, M., M. Beneš, J. Kratochvíl, and P. Pauš. "Numerical Simulations of Glide Dislocations in Persistent Slip Band." Acta Physica Polonica A 128, no. 4 (2015): 506–10. http://dx.doi.org/10.12693/aphyspola.128.506.

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4

Hunsche, A., and P. Neumann. "Quantitative measurement of persistent slip band profiles and crack initiation." Acta Metallurgica 34, no. 2 (1986): 207–17. http://dx.doi.org/10.1016/0001-6160(86)90192-6.

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5

Déprés, Christophe, Christian F. Robertson, Marc Fivel, and Suzanne Degallaix. "A Three Dimensional Discrete Dislocation Dynamics Analysis of Cyclic Straining in 316L Stainless Steel." Materials Science Forum 482 (April 2005): 163–66. http://dx.doi.org/10.4028/www.scientific.net/msf.482.163.

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The early stages of the formation of dislocation microstructures in low strain fatigue are analysed,using three-dimensional discrete dislocation dynamics modelling (DDD). A detailed analysis of the simulated microstructures provide a detailed scheme for the persistent slip band formation, emphasizing the crucial role of cross-slip for both the initial strain spreading inside of the grain and for the subsequent strain localization in the form of slip bands. A new ad-hoc posttreatment tool evaluates the surface roughness as the cycles proceed. Slip markings and their evolutions are analysed, in relation to the dislocation microstructure. This dislocation-based study emphasizes the separate contribution of plastic slip in damage nucleation. A simple 1D dislocation based model for work-hardening in crystal plasticity is proposed. In this model, the forest dislocations are responsible for friction stress (isotropic work-hardening), while dislocation pile-ups and dislocation trapped in Persistent Slip Bands (PSB) produce the back stress (kinematic workhardening). The model is consistent with the stress-strain curves obtained in DDD. It is also consistent with the stress-strain curves experimentally obtained for larger imposed strain amplitudes.

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6

Cordero, L., A. Ahmadieh, and P. K. Mazumdar. "A cumulative fatigue damage formulation for persistent slip band type materials." Scripta Metallurgica 22, no. 11 (1988): 1761–64. http://dx.doi.org/10.1016/s0036-9748(88)80279-5.

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7

Matsuno, Hiroshi. "Characteristics of Complementary Plastic Energy Produced by Hysteresis Curves and Analyses of Microstructures in Fatigued Metals." Key Engineering Materials 340-341 (June 2007): 513–18. http://dx.doi.org/10.4028/www.scientific.net/kem.340-341.513.

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Experimental characteristics of complementary plastic energy produced by a stress-strain hysteresis curve at a saturated stage in low cycle fatigue are investigated for some steels, and mechanical models for analyzing microstructures of fatigued metals are discussed. As a result, it is found that volume of a cell is varied in inverse proportion to plastic strain range: the density of cells is in proportion to plastic strain range. Consequently, the total number of cells is proportional to plastic strain range. This final conclusion is similar to Winter's opinion concerning persistent slip band structures in high cycle fatigue [1] where, although wall spacing of a cell is invariable and inde-pendent of plastic strain range, a region occupied by persistent slip bands increases proportionally to plastic strain range and consequently the number of cells is in proportion to plastic strain range.

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8

Baxter, W. J., and P. C. Wang. "A finite element calculation of the deformation of a persistent slip band." Scripta Metallurgica 22, no. 2 (1988): 207–11. http://dx.doi.org/10.1016/s0036-9748(88)80335-1.

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9

Křišťan, J., and J. Kratochvíl. "Interactions of glide dislocations in a channel of a persistent slip band." Philosophical Magazine 87, no. 29 (2007): 4593–613. http://dx.doi.org/10.1080/14786430701576324.

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10

Cao, Wei-di, and Hans Conrad. "ON THE EFFECT OF PERSISTENT SLIP BAND (PSB) PARAMETERS ON FATIGUE LIFE." Fatigue & Fracture of Engineering Materials and Structures 15, no. 6 (1992): 573–83. http://dx.doi.org/10.1111/j.1460-2695.1992.tb01296.x.

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11

Gregor, V., and J. Kratochvíl. "Self-organization approach to cyclic microplasticity: A model of a persistent slip band." International Journal of Plasticity 14, no. 1-3 (1998): 159–72. http://dx.doi.org/10.1016/s0749-6419(97)00046-6.

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12

Ma, B. T., and C. Laird. "Comments on “A cumulative fatigue damage formulation for persistent slip band type materials”." Scripta Metallurgica 23, no. 6 (1989): 1029–31. http://dx.doi.org/10.1016/0036-9748(89)90291-3.

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13

Polák, Jaroslav, Jiří Man, Tomáš Vystavěl, and Lukáš Zouhar. "Fatigue Crack Initiation in Crystalline Materials – Experimental Evidence and Models." Key Engineering Materials 345-346 (August 2007): 379–82. http://dx.doi.org/10.4028/www.scientific.net/kem.345-346.379.

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Recent observations relevant to the early stages of the fatigue damage of crystalline materials are reviewed. Experimental evidence on the localization of the cyclic plastic strain and on the surface relief formation in cyclic loading of 316L austenitic stainless steel is presented. The focused ion beam is used for exposing three-dimensional evidence of persistent slip markings (PSMs). PSMs consist of extrusions and parallel or alternating intrusions which develop during cyclic loading. Monte Carlo simulations of vacancy generation within persistent slip band (PSB) and their migration to the matrix where they annihilate on the edge dislocations are used to simulate the growth of extrusions and intrusions. The results of the simulations are compared with experimental data and discussed in terms vacancy models of fatigue crack initiation.

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14

KITAMURA, Takayuki, Takashi SUMIGAWA, and Kazuyoshi OISHI. "3-Dimensional Local Stress Field in Copper Polycrystal and Persistent Slip Band under Fatigue." Transactions of the Japan Society of Mechanical Engineers Series A 69, no. 677 (2003): 203–9. http://dx.doi.org/10.1299/kikaia.69.203.

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15

Kochmann, Dennis M., and Klaus Hackl. "Formation of persistent slip band-structures during cyclic loading in finite-strain crystal plasticity." PAMM 10, no. 1 (2010): 301–2. http://dx.doi.org/10.1002/pamm.201010143.

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16

Křištán, Josef, Jan Kratochvíl, Vojtěch Minárik, and Michal Beneš. "Numerical simulation of interacting dislocations glide in a channel of a persistent slip band." Modelling and Simulation in Materials Science and Engineering 17, no. 4 (2009): 045009. http://dx.doi.org/10.1088/0965-0393/17/4/045009.

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17

Baxter, William J., and Pei-Chung Wang. "A finite element model of a persistent slip band based upon electron microscopic evidence." Metallurgical Transactions A 19, no. 10 (1988): 2457–65. http://dx.doi.org/10.1007/bf02645473.

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18

Lavenstein, Steven, Yejun Gu, Dylan Madisetti, and Jaafar A. El-Awady. "The heterogeneity of persistent slip band nucleation and evolution in metals at the micrometer scale." Science 370, no. 6513 (2020): eabb2690. http://dx.doi.org/10.1126/science.abb2690.

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Fatigue damage in metals manifests itself as irreversible dislocation motion followed by crack initiation and propagation. Characterizing the transition from a crack-free to a cracked metal remains one of the most challenging problems in fatigue. Persistent slip bands (PSBs) form in metals during cyclic loading and are one of the most important aspects of this transition. We used in situ microfatigue experiments to investigate PSB formation and evolution mechanisms, and we discovered that PSBs are prevalent at the micrometer scale. Dislocation accumulation rates at this scale are smaller than those in bulk samples, which delays PSB nucleation. Our results suggest the need to refine PSB and crack-initiation models in metals to account for gradual and heterogeneous evolution. These findings also connect micrometer-scale deformation mechanisms with fatigue failure at the bulk scale in metals.

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19

Föckel, H. J., and Th Goldberg. "Role of eigenstresses in the propagation of a persistent slip band nucleus near a free surface." Physica Status Solidi (a) 105, no. 2 (1988): K111—K114. http://dx.doi.org/10.1002/pssa.2211050250.

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20

Šittner, P., V. Novák, and J. Brádler. "Persistent slip band — Grain boundary interactions in low strain fatigue of isoaxial Fe-14wt. %Cr bicrystals." Scripta Metallurgica et Materialia 27, no. 6 (1992): 705–10. http://dx.doi.org/10.1016/0956-716x(92)90492-w.

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21

Meng, Fanshi, Emilie Ferrié, Christophe Déprés, and Marc Fivel. "3D discrete dislocation dynamic investigations of persistent slip band formation in FCC metals under cyclical deformation." International Journal of Fatigue 149 (August 2021): 106234. http://dx.doi.org/10.1016/j.ijfatigue.2021.106234.

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22

Ou, Chun-Yu, and C. Richard Liu. "The Effects of Grain Size and Strain Amplitude on Persistent Slip Band Formation and Fatigue Crack Initiation." Metallurgical and Materials Transactions A 50, no. 11 (2019): 5056–65. http://dx.doi.org/10.1007/s11661-019-05423-6.

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23

Meyers, C. A., and D. S. Grummon. "A finite element model of persistent slip band interaction with strengthened surface films during low cycle fatigue." Materials Science and Engineering: A 130, no. 2 (1990): 127–38. http://dx.doi.org/10.1016/0921-5093(90)90054-7.

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24

Fourel, Lucas, Jean-Philippe Noyel, Etienne Bossy, Xavier Kleber, Philippe Sainsot, and Fabrice Ville. "Towards a grain-scale modeling of crack initiation in rolling contact fatigue - Part 2: Persistent slip band modeling." Tribology International 163 (November 2021): 107173. http://dx.doi.org/10.1016/j.triboint.2021.107173.

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25

Li, Wei. "Review on Surface Failure Mode of Metallic Materials in Very High Cycle Fatigue Regime." Advanced Materials Research 902 (February 2014): 66–69. http://dx.doi.org/10.4028/www.scientific.net/amr.902.66.

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With higher cleanness upgraded steadily, surface failure of metallic materials in very high cycle fatigue (VHCF) regime beyond 107 cycles has been reported one after another. The occurrence of surface crack initiation to failure in VHCF regime is closely related to the following factors: (i) surface finishing condition of specimen, i.e. whether some grinding scratches, grooves and cavities with a relatively larger size than the subsurface defect exist at the surface of specimen; (ii) type, size, location, distribution and density of metallurgical defects such as inclusion contained in the subsurface of material; (iii) degree of persistent slip band (PSB) deformation induced by surface roughening of specimen, mainly corresponding to the some ductile single-phase metallic materials.

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26

Zhong, Wei Hua, Zhen Feng Tong, Zheng Wang, Jin Xu Li, and Wen Yang. "Fatigue Mechanism of Domestic 316LN Stainless Steel in Simulated AP1000 First-Loop Water Environment." Materials Science Forum 913 (February 2018): 247–53. http://dx.doi.org/10.4028/www.scientific.net/msf.913.247.

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Fatigue fracture surfaces and crack morphologies of 316LN stainless steel that test in a simulated AP1000 first-loop water and air environment were investigated by SEM, LSCM and EBSD. The results showed that, the fatigue crack initiated at persistent slip band, impurities and grain boundary, and then propagated in a trans-granular manner with typical fatigue striations. Characteristics of corrosion fatigue, such as brittle fatigue striation, rhomboid corrosion product and the trace of corrosions were found on the fracture surface of first-loop water environment specimen. The strain on first-loop water environment specimen is unevenly distributed surrounding the crack, and the gradient is not obvious, while that on air environment ones is evenly distributed , and the distribution gradient is associated with the distance of crack from . The fatigue crack propagation was accelerated in the first-loop water environment, and the EAC mechanism is most likely to be HIC.

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27

Prasad Reddy, G. V., R. Sandhya, K. Laha, C. Depres, C. Robertson, and A. K. Bhaduri. "The effect of the location of stage-I fatigue crack across the persistent slip band on its growth rate – A 3D dislocation dynamics study." Philosophical Magazine 97, no. 16 (2017): 1265–80. http://dx.doi.org/10.1080/14786435.2017.1294269.

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28

Wang, Dong Ming, Wei Li, Ping Wang, and Wei Xian Chu. "Review on Surface Failure Mode of Metallic Materials in Very High Cycle Fatigue Regime." Advanced Materials Research 652-654 (January 2013): 1295–300. http://dx.doi.org/10.4028/www.scientific.net/amr.652-654.1295.

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With higher cleanness upgraded steadily, surface failure of metallic materials in very high cycle fatigue (VHCF) regime beyond 107 cycles has been reported one after another. The occurrence of surface crack initiation to failure in VHCF regime is closely related to the following factors: (i) surface finishing condition of specimen, i.e. whether some grinding scratches, grooves and cavities with a relatively larger size than the subsurface defect exist at the surface of specimen; (ii) type, size, location, distribution and density of metallurgical defects such as inclusion contained in the subsurface of material; (iii) degree of persistent slip band (PSB) deformation induced by surface roughening of specimen, mainly corresponding to the some ductile single-phase metallic materials. Furthermore, the effect of environment such as humidity also accelerates surface crack initiation and propagation in VHCF regime. In the present paper, the authors briefly reviewed surface failure modes of metallic materials in VHCF regime beyond 107 cycles, and analyzed the surface crack initiation and propagation mechanisms from the viewpoints of the fracture mechanics and statistics.

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29

Shodja, H. M., Y. Hirose, and T. Mura. "Intergranular Crack Nucleation in Bicrystalline Materials Under Fatigue." Journal of Applied Mechanics 63, no. 3 (1996): 788–95. http://dx.doi.org/10.1115/1.2823364.

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During cyclic deformation of polycrystalline materials, as substantiated by many experimental observations, due to existence of high stress concentration at the interfaces the preferential site of crack nucleation is intercrystalline. Accordingly, it is assumed that the highly localized cyclic deformation persistent slip band (PSB) occurs along the grain boundary (GB) which results in intergranular crack initiation. In the present work the irreversible accumulation of dislocations are used to characterize PSB by means of double pile-up which are composed of vacancy and interstitial dipoles. We shall give the mechanism and a quantitative remedy of ratcheting of plastic deformation peculiar to fatigue deformation. In a manner conceptually analogous to Griffith theory (1921), the critical number of cycles to failure and hence the S-N curves for crack initiation is obtained by considering the free energy of the system. The Gibbs free energy change ΔG increases with the fatigue cycle number due to cyclic increment of elastic strain energy which in turn stems from cyclic pile-up of dislocations along the slip planes. The Gibbs free energy change attains its maximum value at a critical cycle number beyond which the state of dislocation dipole accumulation becomes energetically unstable. In our theory we postulate that this critical state is the onset of crack initiation. We shall give a quantitative value for the fatigue limit and analyze the dependence of the S-N curve on several important physical parameters such as grain size; surface energy; yield strength; width of the PSB; and the ratio of the shear modulus of the bicrystalline material.

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30

Weidner, Anja, and Werner Skrotzki. "Persistent Slip Bands." Materials Testing 51, no. 9 (2009): 526–31. http://dx.doi.org/10.3139/120.110065.

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31

Matsuno, Hiroshi. "Fundamental Concepts for Formulating Fatigue Strength Diagrams of Notched Metals." Advanced Materials Research 891-892 (March 2014): 1379–84. http://dx.doi.org/10.4028/www.scientific.net/amr.891-892.1379.

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In the present paper, two fundamental concepts are discussed for formulating fatigue strength diagrams of notched metals. The first is a hypothesis of cyclic plastic adaptation that reflects mechanical behavior/property inherent in a persistent slip band. From this hypothesis, an equivalent cyclic stress ratio , which is the corresponding parameter between the cyclic stress condition of a notched and un-notched specimen, is derived. is extended to multi-axial cyclic stress conditions by use of the potential stress defined by Mises', Kawamoto's criterion, etc. The fatigue strength of a notch specimen is diagramed as a relation between and the notch root stress range . As a result, the fatigue strength is characterized into the two types of and , which can be replaced by the fatigue strength in the surface layer of the un-notch specimen and by the threshold stress of the crack specimen with the same crack depth as the notch depth, respectively. The second idea is how to express parametrically notch size factors based on a notch behavior/property map. For the type of , the notch size factor is expressed by a power function of a square root of a product of a notch root radius and a notch depth , and for the type of as a power function of the notch depth . These factors can be also applied to multi-axial cyclic stress conditions.

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32

Weidner, A., R. Beyer, C. Blochwitz, C. Holste, A. Schwab, and W. Tirschler. "Slip activity of persistent slip bands in polycrystalline nickel." Materials Science and Engineering: A 435-436 (November 2006): 540–46. http://dx.doi.org/10.1016/j.msea.2006.07.039.

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33

Brown, L. M. "Dislocation plasticity in persistent slip bands." Materials Science and Engineering: A 285, no. 1-2 (2000): 35–42. http://dx.doi.org/10.1016/s0921-5093(00)00662-6.

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34

Polák, J., V. Mazánová, M. Heczko, I. Kuběna, and J. Man. "Profiles of persistent slip markings and internal structure of underlying persistent slip bands." Fatigue & Fracture of Engineering Materials & Structures 40, no. 7 (2017): 1101–16. http://dx.doi.org/10.1111/ffe.12567.

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35

Lukáš, P., and L. Kunz ‡. "Role of persistent slip bands in fatigue." Philosophical Magazine 84, no. 3-5 (2004): 317–30. http://dx.doi.org/10.1080/14786430310001610339.

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36

Kubin, Ladislas, and Maxime Sauzay. "Persistent slip bands: Similitude and its consequences." Acta Materialia 104 (February 2016): 295–302. http://dx.doi.org/10.1016/j.actamat.2015.11.010.

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37

Weidner, A., W. Tirschler, C. Blochwitz, and Werner Skrotzki. "The Half-Cycle Slip Activity of Persistent Slip Bands in Polycrystals." Materials Science Forum 567-568 (December 2007): 123–27. http://dx.doi.org/10.4028/www.scientific.net/msf.567-568.123.

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The development of the volume fraction of cumulated persistent slip bands (PSBs) in cyclically deformed nickel polycrystals was investigated in dependence on the number of cycles using scanning electron microscopy (SEM) and atomic force microscopy (AFM). It was shown that there is a large scatter of the volume fraction of PSBs from grain to grain. Three different tendencies for the development of the volume fraction with increasing number of cycles were distinguished. It was shown that there is a correlation of the orientation of the primary slip systems with the volume fraction of cumulated PSBs and the activation of PSBs during half-cycle deformation.

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38

Polák, Jaroslav, Jiří Man, and Ivo Kuběna. "The True Shape of Persistent Slip Markings in Fatigued Metals." Key Engineering Materials 592-593 (November 2013): 781–84. http://dx.doi.org/10.4028/www.scientific.net/kem.592-593.781.

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Persistent slip markings (PSMs) were experimentally studied in 316L steel fatigued to early stages of the fatigue life. High resolution SEM, combined with focused ion beam (FIB) technique and atomic force microscopy (AFM) were used to assess the true shape of PSMs in their early stage of development. General features of PSMs in fatigued metals are extrusions and intrusions. Their characteristic features were determined. They were discussed in relation with the theories of surface relief formation and fatigue crack initiation based on the formation, migration and annihilation of point defects in the bands of intensive cyclic slip - persistent slip bands (PSBs)

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39

Buque, C. "Persistent slip bands in cyclically deformed nickel polycrystals." International Journal of Fatigue 23, no. 6 (2001): 459–66. http://dx.doi.org/10.1016/s0142-1123(01)00013-5.

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40

Brown, L. M. "Dislocation bowing and passing in persistent slip bands." Philosophical Magazine 86, no. 25-26 (2006): 4055–68. http://dx.doi.org/10.1080/14786430500501689.

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41

Brown, L. M. "Cracks and extrusions caused by persistent slip bands." Philosophical Magazine 93, no. 28-30 (2013): 3809–20. http://dx.doi.org/10.1080/14786435.2013.798048.

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42

Schwartz, Julien, Olivier Fandeur, and Colette Rey. "Modelling of Low Cycle Fatigue Initiation of 316LN Based on Crystalline Plasticity and Geometrically Necessary Dislocations." Materials Science Forum 636-637 (January 2010): 1137–42. http://dx.doi.org/10.4028/www.scientific.net/msf.636-637.1137.

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Initiation of intragranular cracks during low cycle fatigue is governed by complex microstructural phenomena. Depending on the loading amplitude, number of cycles, lattice structure and/or chemical composition, different dislocation structures (veins, cells or Persistent Slip Bands) develop and induce heterogeneous localization of strain and stress in the material. For a better comprehension of crack initiation in 316LN stainless steel, low cycle fatigue tests and numerical simulations were performed. Specimens of 316LN steel with polished shallow notch were cycled with constant loading amplitude and Persistant Slip Bands were identified by SEM observations. In parallel, numerical studies were carried out with the model of cristalline plasticity CristalECP. Simulations were performed on 3D polycristalline aggregates of 316LN steel with the finite elements code Abaqus® and Cast3m®. The results show a heterogeneous localization of strain in bands. For a more precise computation of the mechanical fields and to introdruce a grain size effect, Geometrically Necessary Dislocations were introduced in CristalECP. The GNDs are directly related and computed with the lattice curvature.

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43

Zhang, Z. F., Z. G. Wang, and J. Eckert. "What types of grain boundaries can be passed through by persistent slip bands?" Journal of Materials Research 18, no. 5 (2003): 1031–34. http://dx.doi.org/10.1557/jmr.2003.0141.

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Three typical interactions of persistent slip bands (PSBs) with different types of grain boundaries (GBs) were investigated and analyzed in fatigued copper crystals. The results show that PSBs cannot transfer through all types of large-angle GBs, regardless of their orientation with respect to the stress axis. Secondary slip was often observed near the GBs, leading to strain incompatibility. When the slip systems of the two adjacent crystals are coplanar, the transmission of a PSB across a GB strongly depends on the slip directions of the two adjacent crystals. It was found that only the low-angle GBs can be passed through by PSBs, and accordingly they are insensitive to intergranular fatigue cracking. For a special copper bicrystal with coplanar slip systems, the ladderlike dislocation arrangements within the adjacent PSBs become discontinuous and a dislocation-affected-zone appears near the GB due to the difference in the slip direction of the two adjacent crystals. Therefore, the necessary conditions for the transmission of a PSB across a GB are that the neighboring grains have a coplanar slip system and identical slip directions.

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44

Petrenec, Martin, Jaroslav Polák, Tomáš Šamořil, Jiří Dluhoš, and Karel Obrtlík. "In Situ Study of the Mechanisms of High Temperature Damage in Elastic-Plastic Cyclic Loading of Nickel Superalloy." Advanced Materials Research 891-892 (March 2014): 530–35. http://dx.doi.org/10.4028/www.scientific.net/amr.891-892.530.

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In-situ Low Cycle Fatigue test (LCF) at temperature 635 °C have been performed in SEM on flat specimen ofcast Inconel 713LC superalloy. The aim of the investigation was to studymechanisms of the fatigue damage during elastic-plastic cycling by theobservations of the characteristic surface relief evolution and theaccompanying internal dislocation structures. The selected locations on thesurface were systematically studied in-situ and documented by SEM and usingAFM. The surface relief in the first tensile half-cycle was formed by numerousslip steps on the primary slip planes (111). In the following compressionhalf-cycle additional opposite slip were formed. The relief was modified in thenext cycles but without forming additionally new slip traces in the primarysystem. The reorientation of two grains in the gauge area was measured usingEBSD. At the end of cyclic loading the relation between surface persistent slipmarkings and persistent slip bands in the interior of the material wasdocumented by TEM on lamella prepared by FIB. The early stages of extrusion andintrusion formation were documented. The damage mechanism evolution is closelyconnected with the cyclic strain localization to the persistent slip bands thatare also places of fatigue crack initiation.

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45

Trochidis, A. "Formation and evolution of persistent slip bands in metals." Journal of the Mechanics and Physics of Solids 48, no. 8 (2000): 1761–75. http://dx.doi.org/10.1016/s0022-5096(99)00077-0.

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46

Kubin, Ladislas, and Maxime Sauzay. "Persistent slip bands: The bowing and passing model revisited." Acta Materialia 132 (June 2017): 517–24. http://dx.doi.org/10.1016/j.actamat.2017.04.064.

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47

Dodaran, M., M. M. Khonsari, and S. Shao. "Critical operating stress of persistent slip bands in Cu." Computational Materials Science 165 (July 2019): 114–20. http://dx.doi.org/10.1016/j.commatsci.2019.04.036.

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48

Polák, Jaroslav, and Jiří Man. "Cyclic Slip Localization and Crack Initiation in Crystalline Materials." Advanced Materials Research 891-892 (March 2014): 452–57. http://dx.doi.org/10.4028/www.scientific.net/amr.891-892.452.

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Abstract:

Cyclic plastic straining in crystalline materials is localized to persistent slip bands (PSBs) and results in formation of persistent slip markings (PSMs) consisting of extrusions and intrusions. Intensive plastic strain in PSBs results in dislocation interactions and formation of point defects. The extended model based on point defect formation, migration and annihilation is presented describing surface relief formation in the form of extrusion-intrusion pairs. Point defect migration and resulting mass transfer is the principle source of cyclic slip irreversibility leading to crack-like defects - intrusions. Fatigue cracks start in the tip of sharp intrusions.

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49

Aifantis, Elias C. "On the Problem of Dislocation Patterning and Persistent Slip Bands." Solid State Phenomena 3-4 (January 1991): 397–405. http://dx.doi.org/10.4028/www.scientific.net/ssp.3-4.397.

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50

Sedla´cˇek, R. "Internal stresses in dislocation wall structure of persistent slip bands." Computational Materials Science 7, no. 1-2 (1996): 21–26. http://dx.doi.org/10.1016/s0927-0256(96)00055-9.

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