Abstract:Ge implanted with 1 MeV Si + at a dose of 1 ϫ 10 15 cm −2 creates a buried amorphous layer that, upon regrowth, exhibits several forms of defects-end-of-range ͑EOR͒, regrowth-related, and clamshell defects. Unlike Si, no planar ͕311͖ defects are observed. The minimal EOR defects are small dotlike defects and are very unstable, dissolving between 450 and 550°C. This is in contrast to Si, where the EOR defects are very stable. The amorphous layer results in both regrowth-related defects and clamshell defects, wh… Show more
“…2 Recently Hickey et al reported on defect formation and evolution during regrowth of amorphized ion-implanted Ge. 3 They observed regrowth related defects in annealed 1 MeV Si implanted Ge. End of range defects were minimal and annealed out between 450 and 550°C while regrowth defects were more stable.…”
Positron annihilation spectroscopy was used to study defects created during the ion implantation and annealing of Ge. Ge and Si ions with energies from 600 keV to 2 MeV were implanted at fluences between 1 ϫ 10 12 cm −2 and 4 ϫ 10 14 cm −2 . Ion channeling measurements on as-implanted samples show considerable lattice damage at a fluence of 1 ϫ 10 13 cm −2 and a fluence of 1 ϫ 10 14 cm −2 was enough to amorphize the samples. Positron experiments reveal that the average free volume in as-irradiated samples is of divacancy size. Larger vacancy clusters are formed during regrowth of the damaged layers when the samples are annealed in the temperature range 200-400°C. Evolution of the vacancy-related defects upon annealing depends noticeably on fluence of ion implantation and for the highest fluences also on ion species.
“…2 Recently Hickey et al reported on defect formation and evolution during regrowth of amorphized ion-implanted Ge. 3 They observed regrowth related defects in annealed 1 MeV Si implanted Ge. End of range defects were minimal and annealed out between 450 and 550°C while regrowth defects were more stable.…”
Positron annihilation spectroscopy was used to study defects created during the ion implantation and annealing of Ge. Ge and Si ions with energies from 600 keV to 2 MeV were implanted at fluences between 1 ϫ 10 12 cm −2 and 4 ϫ 10 14 cm −2 . Ion channeling measurements on as-implanted samples show considerable lattice damage at a fluence of 1 ϫ 10 13 cm −2 and a fluence of 1 ϫ 10 14 cm −2 was enough to amorphize the samples. Positron experiments reveal that the average free volume in as-irradiated samples is of divacancy size. Larger vacancy clusters are formed during regrowth of the damaged layers when the samples are annealed in the temperature range 200-400°C. Evolution of the vacancy-related defects upon annealing depends noticeably on fluence of ion implantation and for the highest fluences also on ion species.
“…[14][15][16] Recently, some progress in understanding the role of self-interstitials in Ge came from investigations on the migration of B, whose diffusivity is the lowest among all the impurities in Ge.…”
The effect of O implantation in crystalline Ge on the density of native point defects has been investigated through transmission electron microscopy and B diffusion experiments. Annealing at 650• C following O implants produces a band of defects (∼5-10 nm), compatible with GeO 2 nanoclusters (NCs). A clear shape transformation from elongated to spherical forms occurs within 2 h, concomitant with a transient enhanced diffusion of B. A large injection of self-interstitials from GeO 2 NCs, giving a vacancy undersaturation, and a long-range migration of self-interstitials are evidenced and discussed.
“…It should be noted that no threading dislocations or regrowthrelated defects are observed comparing to Si self-ion implantation 14,19 or like recently observed in Ge when amorphized by Si ions where after 650 C anneal a high density of threading dislocations is still present. 20 Moreover, at the anneal temperatures used, no {311} defects are formed. In selfimplanted Si at RT or at 77 K, {311} defects are already formed after annealing at the end of range region.…”
Section: A Buried Amorphous Layermentioning
confidence: 99%
“…Lithiation will then rather easily lead to destabilization of the host Si network (i.e., amorphization) and subsequent formation of new Si x Li y alloy phases, accompanied with significant volume expansion. 25 Crystalline silicon amorphizes at a ratio of 0.3 Li atoms per Si atom, 26 which means for a local Li concentration of 1.5 Â 10 22 at/cm 3 , i.e., far from our implanted maximum of 2.5 Â 10 20 Li/cm 3 . Thus, in the first step of recrystallization, Li atoms must stay in interstitial position and should not play a significant role.…”
The crystalline-to-amorphous transformation induced by lithium ion implantation at low temperature has been investigated. The resulting damage structure and its thermal evolution have been studied by a combination of Rutherford backscattering spectroscopy channelling (RBS/C) and cross sectional transmission electron microscopy (XTEM). Lithium low-fluence implantation at liquid nitrogen temperature is shown to produce a three layers structure: an amorphous layer surrounded by two highly damaged layers. A thermal treatment at 400 C leads to the formation of a sharp amorphous/crystalline interfacial transition and defect annihilation of the front heavily damaged layer. After 600 C annealing, complete recrystallization takes place and no extended defects are left. Anomalous recrystallization rate is observed with different motion velocities of the a/c interfaces and is ascribed to lithium acting as a surfactant. Moreover, the sharp buried amorphous layer is shown to be an efficient sink for interstitials impeding interstitial supersaturation and {311} defect formation in case of subsequent neon implantation. This study shows that lithium implantation at liquid nitrogen temperature can be suitable to form a sharp buried amorphous layer with a well-defined crystalline front layer, thus having potential applications for defects engineering in the improvement of post-implantation layers quality and for shallow junction formation. V C 2013 American Institute of Physics.
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