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Research Papers

Temperature-Dependent Dwell-Fatigue Behavior of Nanosilver Sintered Lap Shear Joint

[+] Author and Article Information
Yansong Tan, Gang Chen

School of Chemical Engineering and Technology,
Tianjin University,
Tianjin 300072, China

Xin Li, Yunhui Mei

School of Material Science and Engineering,
Tianjin University;
Tianjin Key Laboratory of Advanced
Joining Technology,
Tianjin 300072, China

Xu Chen

Mem. ASME
School of Chemical Engineering and Technology,
Tianjin University,
Tianjin 300072, China
e-mail: xchen@tju.edu.cn

1Corressponding author.

Contributed by the Electronic and Photonic Packaging Division of ASME for publication in the JOURNAL OF ELECTRONIC PACKAGING. Manuscript received October 7, 2015; final manuscript received February 15, 2016; published online March 23, 2016. Assoc. Editor: Yi-Shao Lai.

J. Electron. Packag 138(2), 021001 (Mar 23, 2016) (8 pages) Paper No: EP-15-1109; doi: 10.1115/1.4032880 History: Received October 07, 2015; Revised February 15, 2016

A series of dwell-fatigue tests were conducted on nanosilver sintered lap shear joint at elevated temperatures from 125 °C to 325 °C. The effects of temperature and loading conditions on dwell-fatigue behavior of nanosilver sintered lap shear joint were systematically studied. With higher temperature and longer dwell time, creep played a more important part in dwell-fatigue tests. Creep strain accumulated during maximum shear stress hold was found partly recovered by the subsequent cyclic unloading. Both the fracture mode and silver particle growth pattern were characterized by X-ray tomography system and scanning electron microscope (SEM). The mean shear strain rate γ˙m synthesized the effects of various factors, such as temperature, shear stress amplitude, mean shear stress, and dwell time, by which the fatigue and dwell-fatigue life of nanosilver sintered lap shear joint could be well predicted within a factor of two.

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Figures

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Fig. 1

The fixture for sample preparation

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Fig. 2

Schematic loading mode: (a) continuous shear stress cycling, (b) constant loading creep, and (c) maximum and minimum shear stress hold

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Fig. 3

Mean shear strain versus number of cycles (a) without dwell time and (b) with dwell time of 5 s/cycle

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Fig. 4

Fatigue life ratio of tests with 5 s/cycle dwell time and without dwell time at different temperatures

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Fig. 5

At 275 °C, mean shear strain evolution with: (a) different shear stress amplitudes and (b) different mean shear stress

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Fig. 6

At 275 °C: (a) mean shear strain evolution with different dwell time and (b) fatigue life evolution with different dwell time

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Fig. 7

The effect of dwell time on creep life at four temperatures

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Fig. 8

The mean shear strain versus time with peak shear stress hold

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Fig. 9

Microstructure of the fracture sections with dwell time of 5 s/cycle: (a) 125 °C, (b) 225 °C, (c) 275 °C, and (d) 325 °C

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Fig. 10

At test condition of 275 °C, mean shear stress of 3 MPa, shear stress amplitude of 3 MPa, dwell time of 20 s/cycle: (a) three-dimensional (3D) structure of nanosilver paste layer just before failure, (b) the cross section view, (c) microscopy of crack tip, (d) magnification of the area in blue box in (c)

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Fig. 11

The silver particles feature of the fracture sections with dwell time of 5 s/cycle: (a) 125 °C, (b) 225 °C, (c) 275 °C, and (d) 325 °C

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Fig. 12

Mean shear strain rate versus cycles

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Fig. 13

Mean shear strain rate evolution with: (a) different shear stress amplitudes, (b) different dwell time, and (c) different temperatures

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Fig. 14

Fatigue life fitting at 125 °C and 225 °C

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Fig. 15

Comparison between predicted fatigue life and experimental fatigue life

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