The cyclic hardening and saturation behaviour of copper single crystals

Mughrabi, H.

doi:10.1016/0025-5416(78)90174-x

Cited by 628 publications

(194 citation statements)

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“…The cyclic hardening curves of copper single crystals oriented for single, double and multiple slip have been well studied by numerous researchers (Mughrabi 1978, Cheng and Laird 1981, Hong and Laird 1990, Villechaise et al 1991, Gong et al 1995, 1997, Zhang 1995, Li et al 1998b, 1999a. (1991); 6, Li et al (1999a);7, Jin and Winter (1984);8, Zhang (1995); 9, Li et al (1998b);10, Gong et al (1995);11, Jin and Winter (1984); 12, Li et al (1999b);13, Gong et al (1997);14, Li et al (2000b);15, Zhang et al (2000); 16, Li et al (1998b).…”

Section: The Cyclic Hardening Curvesmentioning

confidence: 99%

“…When the plastic shear strain amplitude is larger, the hardening curves may show a softening behaviour (®gure 2). This is particularly true for single-slip single crystals (see ®gure 1 of the paper by Mughrabi (1978)). Some hardening curves show rather complex behaviours; however, in the present paper, as the ®rst approximation, it is assumed that the DBs start to form as the softening occurs.…”

Section: The Cyclic Hardening Curvesmentioning

confidence: 99%

“…Recently, DBs have been frequently observed in fatigued copper single crystals with various orientations. Gostelow (1971) and Mughrabi (1978) found that the DBs analogous to the kink band occurred in single-slip-oriented copper single crystals cyclically deformed at a high strain amplitude of about 10 ¡ 2 . In general, two types of DB, namely DBI and DBII, and occasionally DBIII, have been identi®ed in fatigued copper single crystals (Saletore and Taggart 1978, Jin and Winter 1984, Li et al 1994, Gong et al 1995, 1997, Zhang 1995, Li et al 1998b, 1999a, b, c, 2000b, Zhang et al 2000, where DBI is approximately parallel to the primary slip plane, while DBII makes a certain angle with the primary slip plane.…”

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On the formation of deformation bands in fatigued copper single crystals

Zhang

et al. 2002

Philosophical Magazine A

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A bstractThe features of the deformation bands (DBs) in copper single crystals under cyclic straining were surveyed. A simple model was proposed to account for the formation of DBs. In this model, both crystal rotation and dislocation density variation induced by cyclic straining were considered. The gradual lattice rotation caused by tension and compression irreversibility is the main driving force for the formation of DBs. The drastic release of mobile dislocations resisted by the primary slip bands is the direct trigger for the formation of DBs. From this analysis, one may understand why the formation of DBs is easier in copper single crystals with double-and multiple-slip orientations than that with singleslip orientation. At the same time the e ect of the dislocation avalanche factor on the formation of DBs was discussed.

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Section: The Cyclic Hardening Curvesmentioning

confidence: 99%

Section: The Cyclic Hardening Curvesmentioning

confidence: 99%

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On the formation of deformation bands in fatigued copper single crystals

Zhang

et al. 2002

Philosophical Magazine A

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“…The classical dislocation patterns were systematically found in cyclically saturated Cu single crystals, including vein, persistent slip band (PSB) ladder, PSB wall, labyrinth and cell [2][3][4][5]. Among these dislocation patterns, PSB-ladder structure is most interesting because it corresponds to the existence of the saturation plateau region in the cyclic stress-strain (CSS) curves [6]. Based on previous research, it has been known that although dislocation patterns have all kinds of patterns, their basic feature is the spatial periodically ordered structure with the alternate appearance of dislocation-rich and dislocation-poor regions [7,8].…”

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Basic criterion for the formation of self-organized dislocation patterns in fatigued FCC pure metals

Zhongguang

Zhang

2015

Sci. China Mater.

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tively proposed based on stacking fault energy (SFE).As shown in Fig. 1, PSB ladders or walls are a three-dimensional structure. PSB ladders from t he (12 − 1) plane or PSB walls from the (111) plane occupy about 10% of the PSBs by volume. The walls are 0.03-0.25 μm in thickness with a spacing of about 1.3 μm (see Fig. 2) and they consist of numerous dipoles, especially faulted dipole. The socalled faulted dipole consists of four Shockley partial dislocations and three stacking faults. Th e stair-rods lie at the ends of the stacking fault in the secondary slip plane and their relative position are thus fixed. The dipole as a whole can assume an S-or Z-shaped configuration depending on the position of the Shockley partials. In 1976, Antonopoulos et al. [11,12] pointed out that the matrix vein contained both primary edge dipole and faulted dipole, however, the PSBs were almost full of faulted dipoles, which reflected the microstructure evolution of dislocation patterns. On Based on a large number of experimental results available, it is found that not all the fatigued face-centered-cubic (FCC) pure metals can form the classical persistent slip band (PSB)-ladder structure. The formation of the regular dislocation patterns, especially the PSB ladders, follows one unified principle on the dislocation aggregation and evolution. According to the principle, a simple criterion based on stacking fault energy is proposed to judge whether or not the regular PSB ladders in different FCC pure metals can form.

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“…A large change in mechanical properties is expected when the size of an object is comparable to the characteristic length specific to a primary deformation mechanism. 25 For dislocation-mediated processes, the characteristic length is of the order of 1 m. 26 Twin boundary motion occurs by the motion of twinning disconnections. [27][28][29][30] Disconnections are linear interfacial defects with a Burgers vector component similar to dislocations.…”

Section: Introductionmentioning

confidence: 99%

Deformation twinning in Ni–Mn–Ga micropillars with 10M martensite

Reinhold

Kiener

Knowlton

et al. 2009

Journal of Applied Physics

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The maximum actuation frequency of magnetic shape-memory alloys ͑MSMAs͒ significantly increases with decreasing size of the transducer making MSMAs interesting candidates for small scale actuator applications. To study the mechanical properties of Ni-Mn-Ga single crystals on small length scales, two single-domain micropillars with dimensions of 10ϫ 15ϫ 30 m 3 were fabricated from a Ni-Mn-Ga monocrystal using dual beam focused ion beam machining. The pillars were oriented such that the crystallographic c direction was perpendicular to the loading direction. The pillars were compressed to maximum stresses of 350 and 50 MPa, respectively. Atomic force microscopy and magnetic force microscopy were performed prior to fabrication of the pillars and following the deformation experiments. Both micropillars were deformed by twinning as evidenced by the stress-strain curve. For one pillar, a permanent deformation of 3.6% was observed and ac twins ͑10M martensite͒ were identified after unloading. For the other pillar, only 0.7% remained upon unloading. No twins were found in this pillar after unloading. The recovery of deformation is discussed in the light of pseudoelastic twinning and twin-substrate interaction. The twinning stress was higher than in similar macroscopic material. However, further studies are needed to substantiate a size effect.

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The cyclic hardening and saturation behaviour of copper single crystals

Cited by 628 publications

References 47 publications

On the formation of deformation bands in fatigued copper single crystals

On the formation of deformation bands in fatigued copper single crystals

Basic criterion for the formation of self-organized dislocation patterns in fatigued FCC pure metals

Deformation twinning in Ni–Mn–Ga micropillars with 10M martensite

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