Abstract:The epitaxial regrowth of the implantation-induced amorphous layer in (11̄00)- and (112̄0)-oriented 6H-SiC has been investigated at annealing temperatures below 800 °C using Rutherford backscattering spectrometry and transmission electron microscopy. The surface region of sample is amorphized by the Ar+ ion implantation with an energy of 100 keV at a dose of 2×1015/cm2. The implantation-induced amorphous layer epitaxially regrows at annealing temperatures above 700 °C without the inclusion of other polytype cr… Show more
“…Further epitaxial regrowth is impeded by the nucleation and grain growth of these secondary phases, which leads to a slower reduction of amorphous fraction at 2000 K. However, the behavior of amorphous fraction at 2000 K in the M x model is different from that in the M y model, with a much faster recovery rate, which is consistent with experimental observations in 6H-SiC. 35 The nucleation of secondary ordered phases in the M x model is also observed, but appears only after significant recrystallization has occurred, where the size of the amorphous region is much smaller than that of the original amorphous region. On the other hand, the nucleation of secondary ordered phases in the M y model appears at a very early stage, where the size of the amorphous region is similar to that of the original amorphous region.…”
Section: Recrystallization Along the †0110 ‡ Direction Vs The †121supporting
confidence: 84%
“…Complete recrystallization is reached after about 210 ns at 2000 K. However, it is clear that the formation of secondary ordered phase at the interfaces hinders the SPEG process in 4H-SiC, which may suggest that much higher temperatures are required to completely recover the 4H structure along the ͓0110͔ crystallographic direction than the ͓1210͔ direction. This has been observed experimentally by Satoh et al 35 in 6H-SiC, where the regrowth rate of implantation-induced amorphous layer is faster for ͑1210͒-orientated sample than that for ͑0110͒-orientated sample, or a higher temperature is needed for ͑0110͒-orientated sample to achieve the same regrowth rate. In comparison with the annealing simulations of the M x model ͑Fig.…”
Section: Annealing the M Y Modelsupporting
confidence: 60%
“…42 However, a much higher value of 3.4 eV has been reported for 6H-SiC under other crystallographic orientations. 35 This clearly indicates that the different atomic stacking sequence at the a-c interfaces may have significant effects on the recrystallization mechanisms.…”
Section: Activation Energy Spectrummentioning
confidence: 97%
“…34͒ and 6H-SiC. 35 Zhang et al 10 studied the effects of implantation temperature and ion flux on damage accumulation under Al ion irradiation in 4H-SiC, and the amorphous sample was annealed at a temperature of 450 K. The results suggest that planar defects are generated through the agglomeration of excess Si and C interstitials during postirradiation annealing, and some vacancy clusters are also observed. Solid phase epitaxy of implantation-induced amorphous layer in ͑1210͒-oriented 6H-SiC ͑Ref.…”
Section: Annealing the M X Modelmentioning
confidence: 99%
“…10,12,14,34,35,38 Most of the recrystallization studies have been carried out in 6H-SiC ͑Refs. 10, 12, 14, and 38͒ along ͗0001͘ direction.…”
Section: Recrystallization Along the †0110 ‡ Direction Vs The †121mentioning
The amorphous-to-crystalline transition in 4H-SiC has been studied using molecular dynamics ͑MD͒ methods, with simulation times of up to a few hundred ns and at temperatures ranging from 1000 to 2000 K. Two nanosized amorphous layers, one with the normal of the a-c interfaces along the ͓1210͔ direction and the other along the ͓1010͔ direction, were created within a crystalline cell to study epitaxial recrystallization and the formation of secondary phases. The recovery of bond defects at the interfaces is an important process driving the epitaxial recrystallization of the amorphous layers. The amorphous layer with the a-c interface normal along the ͓1210͔ direction can be completely recrystallized at temperatures of 1500 and 2000 K, but the recrystallized region is defected with dislocations and stacking faults. On the other hand, the recrystallization process for the a-c interface normal along the ͓1010͔ direction is hindered by the nucleation of polycrystalline phases, and these secondary phases are stable for longer simulation times. A general method to calculate activation energy spectra is employed to analyze the MD annealing simulations, and the recrystallization mechanism in SiC consists of multiple stages with activation energies ranging from 0.8 to 1.7 eV.
“…Further epitaxial regrowth is impeded by the nucleation and grain growth of these secondary phases, which leads to a slower reduction of amorphous fraction at 2000 K. However, the behavior of amorphous fraction at 2000 K in the M x model is different from that in the M y model, with a much faster recovery rate, which is consistent with experimental observations in 6H-SiC. 35 The nucleation of secondary ordered phases in the M x model is also observed, but appears only after significant recrystallization has occurred, where the size of the amorphous region is much smaller than that of the original amorphous region. On the other hand, the nucleation of secondary ordered phases in the M y model appears at a very early stage, where the size of the amorphous region is similar to that of the original amorphous region.…”
Section: Recrystallization Along the †0110 ‡ Direction Vs The †121supporting
confidence: 84%
“…Complete recrystallization is reached after about 210 ns at 2000 K. However, it is clear that the formation of secondary ordered phase at the interfaces hinders the SPEG process in 4H-SiC, which may suggest that much higher temperatures are required to completely recover the 4H structure along the ͓0110͔ crystallographic direction than the ͓1210͔ direction. This has been observed experimentally by Satoh et al 35 in 6H-SiC, where the regrowth rate of implantation-induced amorphous layer is faster for ͑1210͒-orientated sample than that for ͑0110͒-orientated sample, or a higher temperature is needed for ͑0110͒-orientated sample to achieve the same regrowth rate. In comparison with the annealing simulations of the M x model ͑Fig.…”
Section: Annealing the M Y Modelsupporting
confidence: 60%
“…42 However, a much higher value of 3.4 eV has been reported for 6H-SiC under other crystallographic orientations. 35 This clearly indicates that the different atomic stacking sequence at the a-c interfaces may have significant effects on the recrystallization mechanisms.…”
Section: Activation Energy Spectrummentioning
confidence: 97%
“…34͒ and 6H-SiC. 35 Zhang et al 10 studied the effects of implantation temperature and ion flux on damage accumulation under Al ion irradiation in 4H-SiC, and the amorphous sample was annealed at a temperature of 450 K. The results suggest that planar defects are generated through the agglomeration of excess Si and C interstitials during postirradiation annealing, and some vacancy clusters are also observed. Solid phase epitaxy of implantation-induced amorphous layer in ͑1210͒-oriented 6H-SiC ͑Ref.…”
Section: Annealing the M X Modelmentioning
confidence: 99%
“…10,12,14,34,35,38 Most of the recrystallization studies have been carried out in 6H-SiC ͑Refs. 10, 12, 14, and 38͒ along ͗0001͘ direction.…”
Section: Recrystallization Along the †0110 ‡ Direction Vs The †121mentioning
The amorphous-to-crystalline transition in 4H-SiC has been studied using molecular dynamics ͑MD͒ methods, with simulation times of up to a few hundred ns and at temperatures ranging from 1000 to 2000 K. Two nanosized amorphous layers, one with the normal of the a-c interfaces along the ͓1210͔ direction and the other along the ͓1010͔ direction, were created within a crystalline cell to study epitaxial recrystallization and the formation of secondary phases. The recovery of bond defects at the interfaces is an important process driving the epitaxial recrystallization of the amorphous layers. The amorphous layer with the a-c interface normal along the ͓1210͔ direction can be completely recrystallized at temperatures of 1500 and 2000 K, but the recrystallized region is defected with dislocations and stacking faults. On the other hand, the recrystallization process for the a-c interface normal along the ͓1010͔ direction is hindered by the nucleation of polycrystalline phases, and these secondary phases are stable for longer simulation times. A general method to calculate activation energy spectra is employed to analyze the MD annealing simulations, and the recrystallization mechanism in SiC consists of multiple stages with activation energies ranging from 0.8 to 1.7 eV.
Hi Nicalon type S (HNS) SiC fiber and 6H-SiC single crystals have been irradiated with 4 MeV Au 3þ at room temperature (RT) and to a fluence of 2 Â 10 15 cm À2 . These irradiation conditions lead to the complete amorphization of the irradiated layer in both samples. Post-irradiation thermal annealing effect on the amorphized samples has been characterized in situ with both Environmental Scanning (E-SEM) and Transmission (TEM) Electron Microscopes. E-SEM observations reveal cracking and exfoliation of the amorphous layer in both samples for temperatures between 850 and 1000 8C. In parallel, TEM observations reveal recrystallization of the amorphous layer in both samples. Even though TEM thin foil specimens did not suffer mechanical failure during the tests, the good agreement between the recrystallization temperatures -870 8C for the single crystal and 900 8C for the HNS fiberplace the recrystallization process as the stress source for the cracking and exfoliation phenomena.Crack detail of a Hi Nicalon type S SiC fiber triggered by the post-irradiation thermal annealing.
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