Halogen lamp rapid thermal annealing of Si- and Be-implanted In0.53Ga0.47As

Halogen lamp rapid thermal annealing was used to activate 100 keV Si and 50 keV Be implants in In_0.53Ga_0.47As for doses ranging between 5 × 10¹²−4 × 10¹⁴ cm⁻². Anneals were performed at different temperatures and time durations. Close to one hundred percent activation was obtained for the 4.1 × 10¹³ cm⁻² Si-implant, using an 850° C/5 s anneal. Si in-diffusion was not observed for the rapid thermal annealing temperatures and times used in this study. For the 5 × 10¹³ cm⁻² Be-implant, a maximum activation of 56% was measured. Be-implant depth profiles matched closely with gaussian profiles predicted by LSS theory for the 800° C/5 s anneals. Peak carrier concentrations of 1.7 × 10¹⁹ and 4 × 10¹⁸ cm⁻³ were achieved for the 4 × 10¹⁴ cm⁻² Si and Be implants, respectively. For comparison, furnace anneals were also performed for all doses.     

Highly conductive buried n+ layers in lnp:fe created by MeV energy Si,S, and Si/S implantation for application to microwave devices

To obtain highly conductive buried layers in InP:Fe, MeV energy Si, S, and Si/ Simplantations are performed at 200°C. The silicon and sulfer implants gave 85 and 100 percent activation, respectively, for a fluence of 8 × 10¹⁴ cm⁻². The Si/S co-implantation also gave almost 100 percent donor activation for a fluence of 8 × 10¹⁴ cm⁻² of each species. An improved silicon donor activation is observed in the Si/S co-implanted material compared to the material implanted with silicon alone. The peak carrier concentration achieved for the Si/S co-implant is 2 × 10¹⁹ cm³. The lattice damage on the surface side of the profile is effectively removed after rapid thermal annealing. Multiple-energy silicon and sulfur implantations are performed to obtain thick and buried n⁺ layers needed for microwave devices and also hyper-abrupt profiles needed for varactor diodes.     

The role of complementary species in P/Be and Ar/Be Co-implanted InP

Chemical and damage effects are used to explain the influence of complementary species on the activation of co-implanted InP. Recently Raoet al. have shown that the damage is the effective mechanism of enhancing activation efficiency and preventing in-diffusion in the P/Be and Ar/Be co-implanted InP. We have confirmed the results and further examined the role of the complementary species by varying their doses. Activation efficiencies as high as 75% and 69.5% were observed in the P/Be and Ar/Be co-implantation, respectively, which can be compared with 31.7% activation in the Be single implantation. Both activation efficiency and in-diffusion decreased as doses of P and Ar increased, that is, as the amount of damage increased. P/Be had always higher activation efficiency than that of Ar/Be when the doses of co-implants are equal. The ratio of the difference in the two activation efficiencies to that of P/Be was the largest at 10¹⁴ cm⁻² of co-implant dose. This behavior was attributed to the chemical effect of the co-implanted P. Photoluminescence results near the band edge showed that the intensity of the main peaks of Be single implantation decreased with increasing P and Ar doses.     

MeV energy sulfur implantation in GaAs and InP

Room temperature and elevated temperature sulfur implants were performed into semi-insulating GaAs and InP at variable energies and fluences. The implantations were performed in the energy range 1–16 MeV. Range statistics of sulfur in InP and GaAs were calculated from the secondary ion mass spectrometry atomic concentration depth profiles and were compared with TRIM92 values. Slight in-diffusion of sulfur was observed in both InP and GaAs at higher annealing temperatures for room temperature implants. Little or no redistribution of sulfur was observed for elevated temperature implants. Elevated temperature implants showed higher activations and higher mobilities compared to room temperature implants in both GaAs and InP after annealing. Higher peak electron concentrations were observed in sulfur-implanted InP (n ≈ 1 × 10¹⁹ cm⁻³) compared to GaAs (n ≈ 2 × 10¹⁸ cm⁻³). The doping profile for a buried n⁺ layer (n ≈ 3.5 × 10¹⁸ cm⁻³) of a positive-intrinsic-negative diode in GaAs was produced by using Si/S coimplantation.     

Si- and Mg-implanted InP,GaInAs and short-time proximity cap annealing

Si- and Mg-ions with energies of 180 keV have been implanted into semi-insulating InP substrates and low doped n- and p-type GalnAs epitaxial layers (3 · l0¹⁶cm⁻³). Sheet resistances and doping profiles are analyzed and compared with LSS theory. Post-implantation annealing is studied with respect to encapsulation, time and temperature. We have tested as new encapsulation techniques for InP the simple proximity cap annealing and for GalnAs the As-doped spun-on SiO₂. Proximity cap annealing yields decomposition-free surfaces when using a recessed capsubstrate. At annealing temperatures of around 800 °C less activation is obtained than with conventional PSG annealing and a surface accumulation of charge-carriers is established. A time limit of around 3 min is found for Si- and Mg-implanted InP, beyond which the sheet resistance no longer decreases and the doping saturates. For Si in InP, short-time annealing yields to a 68 % activation of carriers, not significantly higher than with conventional long-time annealing. In the case of Si in GalnAs, however, short-time annealing is much more effective. A 100 % activation is obtained for a dose of 2.10¹⁴ cm⁻², while only 7 % is found for long annealing. Even at such a high dose of 1. 10¹⁶cm⁻² we have achieved about an order of magnitude higher activation with short annealing than with long annealing. Most information contained in this paper was presented at the 1984 Electron Materials Conference as paper L-l.     

Activation of silicon ion-implanted gallium nitride by furnace annealing

Ion implantation into III–V nitride materials is animportant technology for high-power and high-temperature digital and monolithic microwave integrated circuits. We report the results of the electrical, optical, and surface morphology of Si ion-implanted GaN films using furnace annealing. We demonstrate high sheet-carrier densities for relatively low-dose (n_atoms=5×10¹⁴ cm⁻²) Si implants into AlN/GaN/sapphire heteroepitaxial films. The samples that were annealed at 1150°C in N₂ for 5 min exhibited a smooth surface morphology and a sheet electron concentration n_s ∼9.0×10¹³ cm⁻², corresponding to an estimated 19% electrical activation and a 38% Si donor activation in GaN films grown on sapphire substrates. Variable-temperature Hall-effect measurem entsindicate a Si donor ionization energy ∼15 meV.     

Donor ion-implantation doping into SiC

In this paper, dopant electrical activation and dopant thermal stability results of As and Sb-implanted 6H-SiC epitaxial layers and N ion implantations into bulk semi-insulating (SI) 4H-SiC are presented. In addition, empirical formulas for the first four statistical moments (range, straggle, skewness, and kurtosis) of the implant depth distributions of N and P ion implants are developed in the energy range of 50 keV to 4 MeV. The nitrogen ion-implantations in SI 4H-SiC yield an acceptable (27%) room-temperature electrical activation (ratio of measured sheet carrier concentration at room-temperature to the implant dose) for N concentrations of 2×10¹⁹ cm⁻³. The As and Sb implants out-diffuse during annealing and yield low (<20%) room-temperature electrical activation for implant concentrations of 10¹⁹ cm⁻³. The N and P implant depth distributions in SiC can be simulated using the Pearson IV distribution function and the range statistics provided by the empirical formulas.     

The electrical characteristics of InP implanted with the column IV elements

A study of the electrical characteristics of InP implanted with C, Si, Ge and Sn demonstrates that all of these column IV elements are donors, although the net electrical activation achieved with the light ion C was only about 5%. Samples implanted at temperatures of 150–200°C generally had lower sheet resistivities, higher mobilities and except for high doses, higher sheet carrier concentrations than those done at room temperatures. Implants at 150–200°C with 1 × 10¹⁴cm^?2 of the heavier ions, Si, Ge or Sn, resulted in layers with sheet carrier concentrations of 7.8 × 10¹³, 5.6 × 10¹³ and 4.7 × 10¹³cm^?2, respectively. Carrier concentration profiles of samples implanted at 200°C with 1 × 10¹⁴cm^?2 of Si agreed reasonably well with LSS theory. Higher doses gave rise to substantial diffusion of the implanted Si, whereas room temperature implants showed poor activation near the surface.     

Dose-rate effects in silicon-implanted gallium arsenide from low to high doses

For implantation of silicon dopant into gallium arsenide, sheet resistance and damage increase as the ion dose rate increases in the high-dose regime (>5.0 × 10¹³ cm⁻²). But, in the low-dose regime (<5.0 × 10¹² cm⁻²), although damage still increases with dose rate, the sheet resistance decreases. This qualitative difference implies that there must be a crossover point between the low- and high-dose regimes in the effect of damage and defect formation on dopant activation. This paper describes experiments in which damage and silicon dose were independently varied through the crossover point. Thermal wave, ion channeling, Hall effect measurements, and transmission electron microscopy were used to characterize structural and electrical changes that occur near the crossover. In GaAs implanted with silicon (²⁹Si⁺) at doses between 3 × 10¹² and 6 × 10¹³cm⁻², it is shown that electrical activation for low dose rates first begins to exceed that for high dose rates at a dose of 2 × 10¹³ cm⁻². Rapid growth of Type I dislocations also begins near this same dose, suggesting that there may be a link between defect formation and the crossover to negative dose-rate effects in the high-dose regime.     

Hot-implantation of nitrogen donors into p- type α-SiC and characterization of n+-p junction

N⁺ implantation into p-type a-SiC (6H-SiC, 4H-SiC) epilayers at elevated temperatures was investigated and compared with implantation at room temperature (RT). When the implant dose exceeded 4 × 10₁₅ cm₋₂, a complete amorphous layer was formed in RT implantation and severe damage remained even after post implantation annealing at 1500°C. By employing hot implantation at 500~800°C, the formation of a complete amorphous layer was suppressed and the residual damage after annealing was significantly reduced. For implant doses higher than 10¹⁵ cm⁻², the sheet resistance of implanted layers was much reduced by hot implantation. The lowest sheet resistance of 542Ω/ was obtained by implantation at 500 ~ 800°C with a 4 × 10¹⁵ cm⁻² dose. Characterization of n⁺-p junctions fabricated by N⁺ implantation into p-type epilayers was carried out in detail. The net doping concentration in the region close to the junction showed a linearly graded profile. The forward current was clearly divided into two components of diffusion and recombination. A high breakdown voltage of 615 ∼ 810V, that is almost an ideal value, was obtained, even if the implant dose exceeded 10¹⁵ cm⁻². By employing hot implantation at 800°C, the reverse leakage current was significantly reduced.     

P-type doping of GaAs by carbon implantation

The electrical properties of C-implanted <100> GaAs have been studied following rapid thermal annealing at temperatures in the range from 750 to 950°C. This includes dopant profiling using differential Hall measurements. The maximum p-type activation efficiency was found to be a function of C-dose and annealing temperature, with the optimum annealing temperature varying from 900°C for C doses of 5 × 10¹³ cm⁻² to 800°C for doses ≥5 × 10¹⁴cm⁻². For low dose implants, the net p-type activation efficiency was as high as 75%; while for the highest dose implants, it dropped to as low as 0.5%. Moreover, for these high-dose samples, 5 × 10¹⁵ cm⁻², the activation efficiency was found to decrease with increasing annealing temperature, for temperatures above ∼800°C, and the net hole concentration fell below that of samples implanted to lower doses. This issue is discussed in terms of the amphoteric doping behavior of C in GaAs. Hole mobilities showed little dependence on annealing temperature but decreased with increasing implant dose, ranging from ∼100 cm²/V·s for low dose implants, to ∼65 cm²/V·s for high dose samples. These mobility values are the same or higher than those for Be-, Zn-, or Cd-implanted GaAs.     

Characterization of phosphorus implantation in 4H-SiC

We report the characterization of phosphorus implantation in 4H-SiC. The implanted layers are characterized by analytical techniques (secondary ion mass spectrometry, transmission electron microscopy) as well as electrical and a sheet resistance value as low as 160 Ω/□ has been measured. We have also studied the effect of annealing time and temperature on activation of phosphorus implants. It has been shown to possible to obtain low sheet resistance (∼260 Ω/□) by annealing at a temperature as low as 1200°C. High-dose (∼ 4 × 10¹⁵ cm⁻²) implants are found to have a higher sheet resistance than that on lower dose implants which is attributed to the near-surface depletion of the dopant during high temperature anneal. Different implantation dosages were utilized for the experiments and subsequently junction rectifiers were fabricated. Forward characteristics of these diodes are observed to obey a generalized Sah-Noyce-Shockly multiple level recombination model with four shallow levels and one deep level.     

InP-on-CdS thin film heterostructures

Thin films of InP were deposited on single crystals and thin films of CdS by the planar reactive deposition technique. Good local epitaxy was observed on single crystals of CdS as well as InP and GaAs. The electrical evaluation of unintentionally doped films on semi-insulating InP substrates show them to be n-type with room temperature electron concentrations ranging from 5 × 1016 cm⁻³ to 5 × 10¹⁷ cm⁻³ and mobilities up to 1350 cm²/Vsec. For films intentionally doped with Mn and Be, p-type films were obtained. For Mn doping (deep acceptor level), room temperature mobilities as high as 140 cm²/Vsec and free carrier concentrations as low as 5 × 10¹⁶ cm⁻³ (with dopant level of 3 × 10¹⁸ cm⁻³) were obtained. For Bedoped films, free carrier concentrations of about 5 × 10¹⁸ cm⁻³ and mobilities of 20 cm²/Vsec were found. Scanning electron microscope and microprobe pictures show appreciable interdiffusion between the InP/CdS thin-film pair for InP deposited at 450°C. The loss of Cd from the CdS and the presence of an indium-cadmium-sulfur phase at the InP/CdS interface were observed. Interdiffusion is alleviated for InP deposition at lower temperatures. Supported in part by ERDA and AFOSR.     

The effects of N+ dose in implantation into 6h-sic epilayers

Ion implantation of nitrogen (N) into p-type 6H-SiC {0001} epilayers was investigated as a function of implant dose. Lattice damage induced by implantation was characterized by Rutherford backscattering spectroscopy and Raman scattering. The damage severely increased when the implant dose exceeds 1 x 10¹⁵ cm^-2, and amorphous layers were formed at doses higher than 4 x 10¹⁵ cm^-2. By high-temperature annealing at 1500°C, relatively high electrical activation ratios (≈50%) can be obtained in the case of low-dose implantation (<1 x 10¹⁵cm⁻²). However, the electrical activation showed sharp decrease with increasing implant dose, which may be caused by the residual damage in implanted layers.     

Surface condition of Si implanted GaAs revealed by the noncontact laser/microwave method

The surface recombination of GaAs which has a heavily doped surface layer formed by Si implantation and subsequent annealing has been investigated using the noncontact laser/microwave evaluation method. The experimental results of the samples implanted with doses ranging from 1.0 × 10¹¹ to 3.9 × 10¹² cm⁻² at an energy of 100 keV indicate that the effective surface recombination velocity decreases with dosage because of the heavily doped layer formed after the annealing. On the other hand, the results of the samples implanted with a dose of 3.9 × 10¹² cnr⁻² at energies raging from 50 to 180 keV indicate that the effective surface recombination velocity increases with energy. This is mainly due to the decrease in the peak carrier concentration in the heavily doped layer.     

Temperature-Dependent Studies of Si-Implanted Al<Subscript>0.33</Subscript>Ga<Subscript>0.67</Subscript>N with Different Annealing Temperatures and Times

Electrical activation studies were carried out on Si-implanted Al_0.33Ga_0.67N as a function of ion dose, annealing temperature, and annealing time. The samples were implanted at room temperature with Si ions at 200 keV in doses ranging from 1 × 10¹⁴ cm⁻² to 1 × 10¹⁵ cm⁻², and subsequently proximity-cap annealed from 1150°C to 1350°C for 20 min to 60 min in a nitrogen environment. One hundred percent electrical activation efficiency was obtained for Al_0.33Ga_0.67N samples implanted with a dose of 1 × 10¹⁵ cm⁻² after annealing at either 1200°C for 40 min or at 1300°C for 20 min. The samples implanted with doses of 1 × 10¹⁴ cm⁻² and 5 × 10¹⁴ cm⁻² exhibited significant activations of 74% and 90% after annealing for 20 min at 1300°C and 1350°C, respectively. The mobility increased as the annealing temperature increased from 1150°C to 1350°C, showing peak mobilities of 80 cm²/V s, 64 cm²/V s, and 61 cm²/V s for doses of 1 × 10¹⁴ cm⁻², 5 × 10¹⁴ cm⁻², and 1 × 10¹⁵ cm⁻², respectively. Temperature-dependent Hall-effect measurements showed that most of the implanted layers were degenerately doped. Cathodoluminescence measurements for all samples exhibited a sharp neutral donor-bound exciton peak at 4.08 eV, indicating excellent recovery of damage caused by ion implantation.     

Amorphization and Solid-Phase Epitaxial Growth of C-Cluster Ion-Implanted Si

Amorphization and solid-phase epitaxial growth were studied in C-cluster ion-implanted Si. C₇H₇ ions were implanted at a C-equivalent energy of 10 keV to C doses of 0.1 × 10¹⁵ cm⁻² to 8.0 × 10¹⁵ cm⁻² into (001) Si wafers. Transmission electron microscopy revealed a C amorphizing dose of ~5.0 ×  10¹⁴ cm⁻². Annealing of amorphized specimens to effect solid-phase epitaxial growth resulted in defect-free growth for C doses of 0.5 × 10¹⁵ cm⁻² to 1.0 × 10¹⁵ cm⁻². At higher doses, growth was defective and eventually polycrystalline due to induced in-plane tensile stress from substitutional C incorporation.     

Si-implantation into GaAs grown on Si

200 keV Si implantations were performed in the dose range of 5 × 10¹² − 1 × 10¹⁴ cm⁻² in GaAs grown on Si. For comparison implants were also performed in GaAs layers grown on GaAs substrates. Implanted layers were annealed by both furnace and halogen lamp rapid thermal anneals. Significantly lower donor activations were observed in GaAs layers grown on Si substrates than in the layers grown on GaAs substrates. Extremely low dopant activations were obtained for Be implants in GaAs grown on Si. Photoluminescence and photoreflectance measurements were also performed on the implanted material.     

Thermal activation of shallow boron-ion implants

Boron implanted into n-type Si at 10¹⁵ cm⁻² dose and energies from 500 eV to 1 keV was activated by annealing in nominally pure N₂ and in N₂ with small admixtures of O₂. Effective process times and temperatures were derived by thermal activation analysis of various heating cycles. The lowest thermal budgets used “spike anneals” with heating rates up to 150°C/sec, cooling rates up to 80°C/sec, and minimal dwell time at the maximum temperature. Dopant activation was determined by sheet electrical transport measurements. Surface oxidation was characterized by film thickness ellipsometry. P-n junction depths were inferred from analysis of sheet electrical transport measurements and secondary ion mass spectroscopy profiles. Boron activation increases with boron diffusion from the implanted region. Electrical activation has a thermal activation energy near 5 eV, while boron diffusion has an activation energy near 4 eV. Surface oxide can retard boron diffusion into the ambient for high-temperature anneals.     

Optical and Magnetic Properties of ZnO:V Prepared by Ion Implantation

We report on the optical and magnetic properties of the magnetic semiconductor Zn(V)O fabricated by implantation of 195 keV ₅₁V⁺ ions into bulk ZnO:Al grown by a hydrothermal technique. Two sets of the samples, containing N _d –N _a ∼ 10¹⁵ cm⁻³ and 10¹⁸ cm⁻³, were implanted to doses of 1 × 10¹⁵ cm⁻², 3 × 10¹⁵ cm⁻², and 1 × 10¹⁶ cm⁻². The ion implantation was performed at 573 K. To remove irradiation-induced defects, the samples were annealed in air at 1073 K. Photoluminescence (PL) measurements of Zn(V)O films were carried out at temperatures from 10 K to 300 K. The effects of implantation dose and free carrier concentration on the magnetic properties of Zn(V)O were studied using a superconducting quantum interference device magnetometer. Ferromagnetism has been observed in annealed highly conductive samples implanted to 1 × 10¹⁶ cm⁻². The PL studies of ZnO bulk samples implanted with V⁺ have revealed that thermal annealing at 1073 K restores to a large extent the optical quality of the material. A new emission line centered at 3.307 eV has been found in the PL spectrum of the highly conductive samples implanted to the dose of 1 × 10¹⁶ cm⁻², which is most probably due to complexes involving V ions.