Damage formation and annealing studies of low energy ion implants ...
Damage formation and annealing studies of low energy ion implants ... Damage formation and annealing studies of low energy ion implants ...
The energy spectra have been converted into depth profiles. The profiles for both the NoPAI and PAI samples are shown in Figure 6.4a) and 6.4b) for As and Si, respectively. Figure 6.4 b) shows that the 3 keV As implant produces a ∼11 nm deep amorphous layer, as evidenced by the extra Si scattering yield behind the surface peak that reaches the random level and extends to a depth of ∼11 nm (half height). Arsenic implant profiles for the PAI and NoPAI implants are in close agreement. This is expected since Si is amorphised after a As dose of 10 14 cm -2 (14, chapter 5). MEIS shows that the peak of the As distribution is at 6.3 nm depth, in close agreement with TRIM calculations that yield an Rp = 6.4 nm (profiles not shown). Following a 600 °C 20 min anneal the amorphous layer has recrystallised by SPER. The regrowth is not perfect, leaving a surface damage peak of greater width (5 nm) than the surface peak width of the virgin sample (2.5 nm) and greater height. The As profile too has undergone considerable change with the disappearance from “ beam view” of most of the As in the implanted profile and the appearance of a narrow, segregated As peak with a maximum at a depth of 3 nm. The former is due to As taking up substitutional positions within the regrown Si, where it is no longer visible to the beam. The latter is due to the As concentration that exceeds the solid solubility and cannot be accommodated in the regrown layer due to solid solubility restrictions, although the operation of a simple activated segregation process cannot be excluded. In either case it is “snowploughed” ahead of the advancing amorphous/ crystalline interface and forms the segregated surface peak (7). 125
a) b) c) Yield (counts per 5 µC) Yield (counts per 5 µC) 100 90 80 70 60 50 40 30 20 10 0 0.0 0 2 4 6 8 10 12 14 16 300 250 200 150 100 50 Yield (counts per 5 µC) As depth Depth (nm) 126 3 keV as-impl As 3 keV 600C 20mins As 3 keV 1130C spike As 3 keV as-impl PAI As 3 keV 600C 20mins PAI As 3 keV 1130C spike PAI As 0 0 0 2 4 6 8 Depth (nm) 10 12 14 16 180 160 140 120 100 80 60 40 20 Si depth PAI, 1130C spike anneal virgin as-implanted 600C 20m 1130C spike PAI as-implanted PAI 600C 20m PAI 1130C spike 3.5x10 21 3.0x10 21 2.5x10 21 2.0x10 21 1.5x10 21 1.0x10 21 5.0x10 20 5x10 22 4x10 22 3x10 22 2x10 22 1x10 22 0 0 2 4 6 Depth (nm) 8 10 Figure 6.4 MEIS depth profiles along the [111] blocking direction a) As depth profiles for all the annealed samples. b) Si depth profiles for all the annealed samples. c) Combined depth profile of As, Si and O for the PAI 1130 °C spike annealed sample. As Si O Concentration (at/cm 3 ) concentration (at/cm 3 )
- Page 93 and 94: ackscattering (27). This fact forms
- Page 95 and 96: Figure 4.7 a) Plot of a Gaussian di
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- Page 99 and 100: UP Ion Beam SPIN Rotation Sample Sc
- Page 101 and 102: Kinematic factor (K) 1.0 0.8 0.6 0.
- Page 103 and 104: Figure 4.14 Illustration of the dou
- Page 105 and 106: 4.2.2.4 Interpretation of spectra A
- Page 107 and 108: with are comparatively small, ~ 0.5
- Page 109 and 110: Inelastic energy loss (eV/Ang) 32 2
- Page 111 and 112: iterative procedure is carried out
- Page 113 and 114: Yield (couts per 5µC) 300 250 200
- Page 115 and 116: SIMS experiments were also carried
- Page 117 and 118: MEIS, using the scattering conditio
- Page 119 and 120: 4.5 Sample production Samples have
- Page 121 and 122: an N2/O2 environment to maintain an
- Page 123 and 124: 38 M. Anderle, M. Barozzi, M. Bersa
- Page 125 and 126: damage evolution behaviour observed
- Page 127 and 128: Yield (counts per 5 µC) 250 200 15
- Page 129 and 130: essentially a “zero dose” profi
- Page 131 and 132: no longer “visible” in MEIS has
- Page 133 and 134: yield (cts / 5µC) 500 400 300 200
- Page 135 and 136: 5.4 Conclusion MEIS analysis with a
- Page 137 and 138: Chapter 6 Annealing studies 6.1 Int
- Page 139 and 140: 6.2.2.2 Results and Discussion Figu
- Page 141 and 142: theory predictions and X-ray fluore
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- Page 147 and 148: greater than MEIS. SIMS is not sens
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- Page 153 and 154: a) b) Yield (counts per 5 µC) Yiel
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- Page 157 and 158: duration, is observed. MEIS results
- Page 159 and 160: Yield (counts per 5µC) 500 400 300
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- Page 163 and 164: underneath the SiO2 layer, iii) it
- Page 165 and 166: R s (Ω/sq) 950 900 850 800 750 60
- Page 167 and 168: As concentration (at/cm 3 ) 1E22 1E
- Page 169 and 170: R s (Ω/sq) 950 900 850 800 750 70
- Page 171 and 172: Following annealing it was observed
- Page 173 and 174: ∆a/a (x 10 -3 ) 4,0 epi550 3,5 3,
- Page 175 and 176: Yield (counts per 5 uC) 350 300 250
- Page 177 and 178: (FWHM). Concomitantly, As in the re
- Page 179 and 180: Yield (counts per 5 µC) 450 400 35
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- Page 183 and 184: ecomes steeper for the sample annea
- Page 185 and 186: Figure 6.28 Schematic illustrations
- Page 187 and 188: and the 2D picture in Figure 6.31b)
- Page 189 and 190: 6.5 Conclusion In summary, in this
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- Page 193 and 194: egarding B profiles relevant to the
The <strong>energy</strong> spectra have been converted into depth pr<strong>of</strong>iles. The pr<strong>of</strong>iles for both<br />
the NoPAI <strong>and</strong> PAI samples are shown in Figure 6.4a) <strong>and</strong> 6.4b) for As <strong>and</strong> Si,<br />
respectively. Figure 6.4 b) shows that the 3 keV As implant produces a ∼11 nm deep<br />
amorphous layer, as evidenced by the extra Si scattering yield behind the surface peak<br />
that reaches the r<strong>and</strong>om level <strong>and</strong> extends to a depth <strong>of</strong> ∼11 nm (half height). Arsenic<br />
implant pr<strong>of</strong>iles for the PAI <strong>and</strong> NoPAI <strong>implants</strong> are in close agreement. This is<br />
expected since Si is amorphised after a As dose <strong>of</strong> 10 14 cm -2 (14, chapter 5). MEIS<br />
shows that the peak <strong>of</strong> the As distribut<strong>ion</strong> is at 6.3 nm depth, in close agreement with<br />
TRIM calculat<strong>ion</strong>s that yield an Rp = 6.4 nm (pr<strong>of</strong>iles not shown). Fol<strong>low</strong>ing a 600 °C<br />
20 min anneal the amorphous layer has recrystallised by SPER. The regrowth is not<br />
perfect, leaving a surface damage peak <strong>of</strong> greater width (5 nm) than the surface peak<br />
width <strong>of</strong> the virgin sample (2.5 nm) <strong>and</strong> greater height. The As pr<strong>of</strong>ile too has<br />
undergone considerable change with the disappearance from “ beam view” <strong>of</strong> most <strong>of</strong><br />
the As in the implanted pr<strong>of</strong>ile <strong>and</strong> the appearance <strong>of</strong> a narrow, segregated As peak with<br />
a maximum at a depth <strong>of</strong> 3 nm. The former is due to As taking up substitut<strong>ion</strong>al<br />
posit<strong>ion</strong>s within the regrown Si, where it is no longer visible to the beam. The latter is<br />
due to the As concentrat<strong>ion</strong> that exceeds the solid solubility <strong>and</strong> cannot be<br />
accommodated in the regrown layer due to solid solubility restrict<strong>ion</strong>s, although the<br />
operat<strong>ion</strong> <strong>of</strong> a simple activated segregat<strong>ion</strong> process cannot be excluded. In either case it<br />
is “snowploughed” ahead <strong>of</strong> the advancing amorphous/ crystalline interface <strong>and</strong> forms<br />
the segregated surface peak (7).<br />
125