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The Effect of Sub-boundaries on the Performance and Reliability of ovel SLS ELA<br />
Polysilicon TFTs<br />
M. A. Exarchos 1* , D. C. Moschou 2 , D. N. Kouvatsos 2 , G. J. Papaioannou 1 and A. T. Voutsas 3<br />
1 Physics Department, National and Kapodistrian University of Athens, Athens 15784, Greece<br />
2 Institute of Microelectronics, NCSR Demokritos, Agia Paraskevi 15310, Greece<br />
3 LCD Process Technology Laboratory, Sharp Labs of America, 5700 NM Pacific Rim Blvd, Camas, WA 98607, USA<br />
*mexarcho@phys.uoa.gr<br />
Abstract Polysilicon TFTs fabricated in a film crystallized with a novel SLS ELA technique, yielding rectangular crystal<br />
domains much larger than the TFT channel dimensions, were investigated. The TFT channels were oriented both along the<br />
preferential direction and vertical to it, thus probing the sub-boundary effects of both directions. DLTS assessment was<br />
conducted on unstressed TFTs in order to probe the film’s defect nature. DC hot carrier stress was applied for both channel<br />
orientations, in order to elucidate the effect of the crystallization procedure and its resulting microstructure on the reliability<br />
of the devices. A dimensional optimization of the TFTs was found.<br />
1. Introduction<br />
In this work we investigate the application of a novel SLS ELA polysilicon crystallization method [1-3], termed MN,<br />
for top gate TFTs oriented along both preferential and non-preferential directions. Through DLTS analysis the defect nature<br />
of the polysilicon film is probed. The relation between process characteristics and device reliability is elucidated through hotcarrier<br />
stress. An optimization of the TFT performance through variation of the channel length was attempted.<br />
2. Experimental<br />
The TFTs studied were fabricated in polysilicon film formed by ELA crystallization of a:Si, using an SLS technique<br />
termed MN. In this procedure the mask (Fig. 1) consists of sets of slits orthogonal to each other. The grains grow first in the<br />
Y direction (via the "M" patterns) and, then, sub-boundaries within these grains are swept in the X direction (via the "N"<br />
patterns), which is therefore the preferential direction. This results in large domain sizes but of lower intragrain quality than<br />
other, multi-shot techniques. A SEM image of the polysilicon film can be seen in Fig. 2. Since the crystal domain is much<br />
larger than the TFT channel, no hard grain boundaries should be included in either direction. However, nanoscale subboundaries<br />
(evidenced by features like protrusions and hillocks) are present in both directions, known to affect the TFT<br />
performance [3]. DLTS assessment was conducted on unstressed TFTs, immediately after the device transition from OFF- to<br />
ON-state. Drain current spectra I d (T) were monitored and measured. Devices were stressed and characterized in both<br />
directions. The hot-carrier stress was applied for a maximum duration of 16 hours.<br />
3. Results and Discussion<br />
DLTS measurements were conducted under the same bias conditions for unstressed TFTs. DLTS spectra magnitudes<br />
I d (T) are considerably higher for the devices having the channel aligned to X direction, than in Y direction. This is so<br />
because the respective energy barrier height E B of the grain boundaries is lower (Fig. 3) [4]. For X-oriented TFTs,<br />
E B (X)=0.026eV and for Y-oriented ones, E B (Y)=0.043eV. Further decomposed, the DLTS spectra for each oriented TFT<br />
disclosed three thermally activated contributions corresponding to three discrete traps (Fig. 4). Their activation energies were<br />
calculated in the range 0.39eV-0.53eV. The Arrhenius signatures closest to the detected defects are associated with hole traps<br />
originating from dislocations and rapid thermal annealing (RTA) defects.<br />
To probe the effect of the sub-boundaries on the reliability of our TFTs we applied hot-carrier stress, with<br />
V gstress =V dstress /2, on both channel orientations. A more severe degradation in the X orientation is revealed even for milder<br />
stress conditions (Fig. 5), due to the softer grain boundaries. Also, the parallel shift of the I DS -V GS characteristics in the Y<br />
direction is attributed to charges injected in the gate oxide, while in the X direction the curve distortion implies severe<br />
interface degradation.<br />
In Figs. 6, 7 we see that for channel lengths larger or smaller than 1.2m the performance seems to deteriorate. The<br />
increasing S with increasing L is attributed to more sub-boundaries included within the channel, while its increase with<br />
decreasing L is an electrical effect, ascribed to the increased channel charge in the subthreshold regime [5] due to the<br />
additional drain bias control of the channel region. These two mechanisms define the optimum TFT channel length for our<br />
crystallization process.<br />
4. Conclusions<br />
SLS ELA polysilicon TFTs fabricated in films crystallized with a novel SLS ELA technique termed MN yielding<br />
large rectangular crystal domains were studied, with the TFT channels oriented along the preferential and the non-preferential<br />
direction. The DLTS analysis of the devices showed larger energy barrier height in the Y direction. Discrete traps deep in<br />
polysilicon energy gap were detected, originating from dislocations and rapid thermal annealing defects. TFT degradation<br />
seemed to be less pronounced in the Y direction, due to the harder sub-boundaries obstructing the stress current. The main<br />
degradation mechanism for the X direction was interface state generation, while for the Y direction the gate oxide charge<br />
injection. An optimum channel length was found, defined both by the sub-boundary characteristics and by electrical effects.<br />
References<br />
[1] A.T. Voutsas, IEEE Trans. Electron Dev. ED-50 (2003) 1494.<br />
[2] M.A. Crowder, M. Moriguchi, Y. Mitani and A.T. Voutsas, Thin Solid Films 427 (2003) 101.<br />
[3] A.T. Voutsas, A. Limanov and J.S. Im, J. Appl. Phys. 94 (2003) 7445.<br />
[4] Y.Morimoto et al, Journal of Electrochemical Society, 144, 7, pp 2495-2501, (1997)<br />
[5] A. G. Lewis et al, IEDM '89 Proc., pp. 349-352 (1999).<br />
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