1. Introduction
Solar/visible-blind detection is vital for a number of critical applications including missile plume detection, flame/engine monitoring, chemical/biological agent sensing, and covert space-to-space communications Reference Carrano, Li, Grudowski, Dupuis and Campbell[1]. With its wide bandgap and intrinsic visible-blind absorption spectrum, AlxGa1−xN ternary alloy is the most promising material system for high-performance solar/visible-blind photodetectors Reference Razeghi and Rogalski[2]. High-performance ultraviolet (UV) detectors were reported using AlGaN-based Schottky Reference Monroy, Calle, Pau, Sanchez, Munoz, Omnes, Beaumont and Gibart[3] Reference Rumyantsev, Pala, Shur, Gaska, Levinshtein, Adivarahan, Yang, Simin and Asif Khan[4] Reference Biyikli, Kartaloglu, Aytur, Kimukin and Ozbay[5] Reference Biyikli, Aytur, Kimukin, Tut and Ozbay[6], MSM Reference Yang, Lambert, Li, Collins, Wong, Chowdhury, Dupuis and Campbell[7] Reference Chen, Chang, Su, Chi, Chi, Chang, Sheu and Chen[8] Reference Seo, Lee, Kang, Huang, Doolittle, Jokerst, Brown and Brooke[9], pin Reference Tarsa, Kozodoy, Ibbetson and Keller[10], Reference Collins, Chowdhury, Wong, Yang, Beck, Dupuis and Campbell[11], and avalanche type of photodiodes (PDs) Reference Carrano, Lambert, Eiting, Collins, Li, Wang, Yang, Beck, Dupuis and Campbell[12]. These devices consisted of conventional, single-pass detector structures. On the other hand, resonant cavity enhanced (RCE) detector structure offers selective enhancement of device responsivity Reference Unlu and Strite[13]. The RCE-PD exhibits a multi-pass detection scheme at the cavity resonance wavelengths, which leads to improved efficiency performance.
High performance infrared RCE-PDs using AlGaAs and InGaAs material systems were previously reported Reference Ozbay, Kimukin, Biyikli, Aytur, Gokkavas, Ulu, Unlu, Mirin, Bertness and Christensen[14] Reference Biyikli, Kimukin, Aytur, Gokkavas, Unlu and Ozbay[15] Reference Kimukin, Biyikli, Butun, Aytur, Unlu and Ozbay[16]. Recently, Kishino et al. have demonstrated the first UV RCE-PD with an AlGaN-based MSM PD, where they have reported resonant peaks around 360 nm Reference Kishino, Yonemaru, Kikuchi and Toyoura[17]. In this paper, we report on the design, fabrication, and characterization of high-speed RCE AlGaN Schottky PDs. Au and ITO-Schottky devices were fabricated and compared in terms of detector performance. A peak responsivity of 0.153 A/W at 337 nm and a 3-dB bandwidth of 780 MHz were obtained with ITO and Au-Schottky RCE-PDs respectively.
2. Experimental
2.1 Epitaxial Design
For the design of the RCE-PD structure, a transfer-matrix-method (TMM) based simulation program was used. The detector was designed to achieve a resonant enhancement around 350 nm. The spectral complex refractive index data of AlxGa1−xN needed for the simulations were obtained from Ref. 18. Figure 1 shows the epitaxial layer structure of the designed RCE-PD wafer. A lightly doped (n=5×1016 cm−3) 70 nm thick GaN absorption layer was used as the detector active region. All other detector layers consisted of AlxGa1−xN layers with Al mole fraction larger than 20%. The bottom mirror of the resonant cavity was formed by a 20 pair AlN/Al0.2Ga0.8N DBR. The Bragg mirror was centered at the operation wavelength of λ=360 nm. The λ/4 layer thicknesses required for a highly reflecting AlN/Al0.2Ga0.8N quarter wave stack at this wavelength were determined as 43.3 nm and 36.7 nm respectively. Since the cut-off wavelength of Al0.2Ga0.8N is around 330 nm, all cavity layers except the GaN absorption layer were transparent for λ ≥ 330 nm. The 300 nm thick, highly doped (n=2×1018 cm−3) Al0.2Ga0.8N layer was designed as the ohmic contact layer. To electrically isolate the device mesas, a 200 nm thick undoped Al0.2Ga0.8N layer was grown above the bottom DBR.
Epitaxial layer structure of the designed AlGaN RCE Schottky PD.
2.2 Device Fabrication
The AlGaN/GaN epitaxial layers were grown on a sapphire substrate using MOCVD. The devices were fabricated using a microwave compatible fabrication process consisting of five mask levels: ohmic contact formation, mesa isolation, Schottky contact formation, surface passivation, and metalization of interconnect pads. First, the ohmic contacts were defined via reactive ion etching (RIE) under CCl2F2 plasma, 20 sccm gas flow-rate and 100 W RF power. A controlled etch was done to stop within the n+ Al0.2Ga0.8N layer. The final etch depth was ~0.35 μm. Afterwards Ti/Al contacts were deposited using thermal evaporation and standard lift-off process. The contacts were annealed at 600 oC for 60 seconds in a rapid thermal annealing (RTA) system. Mesa structures of the devices were formed via the same RIE process, by etching all the layers down to the undoped mesa isolation layer. Third step was the deposition of the Schottky contact layer. Au and ITO were used for making Schottky contacts to GaN. ~100 nm thick ITO and ~10 nm thick Au films were RF-sputtered and thermally evaporated on different samples respectively. The ITO films were etched to define the contact regions using dilute HF:H20 solution, whereas the Au films were lifted-off in acetone solution. Next, to passivate the sample surface and protect the Schottky contacts, a ~120 nm thick Si3N4 film was deposited onto the samples by plasma-enhanced-chemical-vapor-deposition (PECVD). Finally, a ~ 0.7 μm thick Ti/Au interconnect metal was deposited and lifted-off to connect the Schottky layers to coplanar waveguide transmission line pads.
2.3 Device Testing
After device fabrication, current-voltage (I-V), spectral responsivity, and high-speed characterizations were carried out. Before device fabrication, reflectivity characterization was made and the results were compared with the simulation results to estimate the actual layer thicknesses. The spectral reflectivity measurements were done using a fiber-optic based setup. Ocean Optics PC2000-UV-VIS PC Plug-in Fiber Optic Spectrometer was used in this measurement, which operated in the 200-850 nm wavelength region. The I-V characterization was carried out using a Hewlett Packard HP4142B DC parametric measurement instrument, DC probes with triax output and low-noise triax cables. Spectral responsivity measurements were done using a 175 W xenon light-source, 1/4 m Digikrom DK240 monochromator, multi-mode UV fiber, DC voltage source, SR830 DSP lock-in amplifier and a Newport model 1830-C calibrated optical power-meter. Xenon lamp output was fed into the monochromator. The monochromator output was chopped and coupled to the fiber using a UV-enhanced focusing lens. The detectors were illuminated by the optical output coming out from the fiber which was calibrated using a NIST-calibrated Si photodetector. The resulting photocurrent was measured using the lock-in amplifier. Temporal high-frequency measurements were done at 357 nm. UV pulses with sub-picosecond pulsewidths were generated using second harmonic generation (SHG) process. A Coherent Mira 900F model femtosecond mode-locked Ti:sapphire laser was used to generate the pump beam at 714 nm. The pump pulses were produced with 76 MHz repetition rate and 140 fs pulse duration. These pulses were frequency doubled to generate a second harmonic beam at 357 nm using a 0.5 mm thick type-I β-BaB2O4 (BBO) crystal. The resulting 357 nm pulses had pulsewidths below 1 ps and were focused on-to the devices using UV-enhanced mirrors and lenses. To measure the pulse response of the detectors at 267 nm, another BBO crystal was added to this setup. Using the pump beam at 800 nm, 267 nm pulses were generated by sum frequency generation process Reference Biyikli, Kartaloglu, Aytur, Kimukin and Ozbay[18]. The detectors were biased using a DC voltage source and a 40 GHz bias-tee. The resulting temporal pulse responses were observed on a 50 GHz sampling oscilloscope.
3. Results and Discussion
In order to estimate the actual epitaxial layer thicknesses, spectral reflectivity was measured before device fabrication. Comparing the measured spectral reflectivity with the simulation results of the ideal detector structure, significant differences between the experimental and computational data were observed. Our original simulations predicted a highly reflective mirror between 340 and 380 nm. However, the experimental reflectivity data showed that the long wavelength edge of the mirror had blue-shifted nearly 25 nm towards 355 nm. This result convinced us that the layers were grown shorter than the original design. Figure 2 shows the reflectivity measurements along with the simulation results obtained with ~10% shorter cavity and mirror layers. With this modified epitaxial layer structure, a reasonable agreement between the experimental and theoretical reflectivity was achieved. A blue-shifted peak reflectivity of 52% around 345 nm was measured.
Measured and simulated spectral reflectivity of the RCE-PD wafer.
The fabricated AlGaN RCE Schottky PDs exhibited low dark currents at small reverse bias values. Both Au and ITO-Schottky samples had dark currents below 10 pA at reverse bias of 1.5 V. Typical breakdown voltages measured were around 10 V, and ITO devices showed larger turn-on voltages than Au devices (Figure 3). The measured dark current density of a 100×100 μm2 RCE ITO-Schottky PD is plotted in Figure 4. 1.3×10−8 A/cm2 dark current density was obtained at 1 V reverse bias.
Typical I-V characteristics of 100x100 μm2 Au and ITO-Schottky RCE-PDs.
Measured dark current density of a 100×100 μm2 ITO-Schottky PD.
The spectral photoresponse measurements of the AlGaN RCE-PDs were performed in the 320-420 nm spectral region. Figure 5 shows the measured spectral quantum efficiency of Au and ITO-Schottky RCE-PDs under different bias conditions. When no reverse bias voltage was applied, peak efficiencies of 20% and 7% were measured with ITO and Au samples respectively. Photoresponse of both samples increased with reverse bias. ITO-Schottky PDs exhibited a resonant peak of 56% at 337 nm under 1 V reverse bias. A weaker resonance was observed in Au-Schottky sample with a peak efficiency of 19% at 350 nm under 4 V reverse bias.
Measured spectral quantum efficiency of Au and ITO-Schottky RCE-PDs.
The difference in the peak responses for ITO and Au-Schottky devices can be explained by two factors: absorption in Schottky layer and matching of top mirror reflectivity. Absorption in Schottky layer directly decreases the achievable peak efficiency. Our simulations predicted that a 100 Å thick Au film absorbed ~356% of incident radiation around 350 nm, whereas for a 100 nm thick ITO layer this loss was ~156%. Top mirror reflectivity plays an important role for optimum RCE operation. In an RCE-PD, enhancement is best observed when R1 = R2e−2αd condition is satisfied, where R1 , R2 , and α corresponds to the top mirror reflectivity, bottom mirror reflectivity, and absorption coefficient of the active layer respectively. In our experiment, with R2 ≈ 52%, maximum enhancement is achieved with 146% and 126% top mirror reflectivity at 350 nm and 337 nm. ITO film displays a reflectivity of ~16% which was close to the optimum value of 126%. Reflectivity of Au film (346% at 350 nm), however, deviated significantly from the optimum condition, resulting in a weaker RCE effect. Figure 6 shows the measured spectral responsivity curves with peak values of 153 mA/W and 46 mA/W for biased ITO and Au-Schottky samples respectively. UV/visible rejection performance of ~1000 and ~600 were measured for ITO and Au-Schottky PDs.
High-speed measurements were performed at two different wavelengths: 357 nm (near-resonance wavelength) and at 267 nm. At both wavelengths, both RCE Schottky PD samples exhibited short rise times and longer decay times. We have measured and analyzed the temporal pulse responses as a function of applied reverse bias voltage, active device area, measurement wavelength, and Schottky contact material.
Spectral responsivity curves of biased Au and ITO-Schottky RCE-PD samples.
Figure 7 shows the bias dependence of high-speed responses obtained with Au-Schottky PDs measured at 357 nm. Faster responses with higher peak amplitudes were measured with increasing reverse bias voltages. Under low bias voltages, some part of the undoped GaN/Al0.2Ga0.8N layers were not depleted, resulting in a diffusion current component. This diffusion component is observed as a slowly decaying tail in the pulse response. As the undoped layers were totally depleted under higher reverse bias voltages, carrier diffusion was eliminated and all the photo-generated carriers were swept towards the contact layers, resulting in faster pulse responses with shorter decaying tails. For a 150×150 μm2 device, full-width-at-half-maximum (FWHM) decreased from 870 ps to 314 ps as applied reverse bias increased from 2 V to 15 V.
Pulse response of a 150x150 μm2 Au-Schottky RCE-PD as a function of reverse bias.
The area dependence of the measured high-speed performance of the Schottky PDs was in parallel to our expectations. Theoretically, better high-speed performance should be achieved with smaller device areas, due to smaller capacitance, and therefore smaller RC time constants. This was the case observed in our measurements. For Au-Schottky PDs, as the device diameter was changed from 200 μm to 30 μm, FWHM decreased from 333 ps to 77 ps at 15 V reverse bias. A similar behavior was observed for ITO-Schottky PDs, which exhibited slower responses with a minimum FWHM of 154 ps at 357 nm. Figure 8(a) and (b) show the area dependence of the 357 nm pulse response for Au and ITO-Schottky devices respectively.
The area dependence of pulse responses measured at 357 nm. (a) Au-Schottky RCE-PD
The area dependence of pulse responses measured at 357 nm. (b) ITO-Schottky RCE-PD
The high-speed measurements at 267 nm resulted in slower pulse responses. This was an expected result, since the Al0.2Ga0.8N cavity layers were not transparent at this wavelength. In this case, additional drift and diffusion currents are generated within the Al0.2Ga0.8N cavity layers, resulting in longer response times. Figure 9(a) and (b) show the measured pulse responses under 267 nm illumination as a function of detector area. The fastest pulse-response obtained at this wavelength had pulse-widths of 110 ps and 234 ps for Au and ITO samples respectively. Figure 10(a) and (b) compares the pulse-widths obtained from Au and ITO RCE-PDs respectively measured at 357 nm and 267 nm.
Temporal pulse responses as a function of device areas measured at 267 nm. (a) Au-Schottky RCE-PD.
Temporal pulse responses as a function of device areas measured at 267 nm. (b) ITO-Schottky RCE-PD
Measured pulse-width variation with device area under 357 nm and 267 nm illumination. (a)Au-Schottky RCE-PD .
Measured pulse-width variation with device area under 357 nm and 267 nm illumination. (b) ITO-Schottky RCE-PD.
Comparing the measurement results obtained with Au and ITO-Schottky PDs, Au-Schottky PD samples exhibited better high-speed performance. To make a comparative analysis, the fastest pulse responses obtained from 30 μm Au and ITO-Schottky devices are normalized and plotted in Figure 11. The rise (charging) portion of the response for Au and ITO samples are very similar, both having short rise times. However, the decay (discharging) parts are drastically different. ITO-Schottky response shows a slower decay when compared to Au-Schottky response. Such a longer fall time indicates a higher RC time constant for ITO devices. Since the capacitance is the same for both devices, the difference in the response should originate from the total device resistance. ITO is known as transparent conductor, however when compared with Au, ITO is a weaker conductor with higher resistivity Reference Biyikli, Kimukin, Aytur, Gokkavas, Unlu and Ozbay[15] Reference Wohlmuth, Seo, Fay, Caneau and Adesida[19]. This leads to a significantly higher series resistance in the device. It is this additional series resistance that increases the RC time constant of ITO-Schottky samples, resulting in longer decay times and slower pulse responses. The corresponding frequency responses are calculated using fast-Fourier transform (FFT) (see inset figure). 3-dB bandwidths of 150 MHz and 780 MHz were achieved for ITO and Au-Schottky PDs respectively. These results are the first high-speed results reported for visible-blind AlGaN RCE-PDs.
Normalized pulse responses of 30 μm-diameter Au and ITO-Schottky RCE-PDs with 77 ps and 154 ps FWHM respectively. Inset shows the corresponding FFT curves.
4. Conclusions
In summary, we have demonstrated high-speed, visible-blind RCE Schottky PDs on AlGaN epitaxial layers. AlGaN RCE-PDs with Au and ITO Schottky layers were fabricated. In spite of the lower-than-expected bottom Al0.2Ga0.8N/AlN Bragg mirror reflectivity, RCE effect was observed in both samples. ITO-Schottky samples displayed higher resonant peaks with a maximum peak responsivity of 0.153 A/W at 337 nm. Au-Schottky samples exhibited faster pulse responses with a minimum pulsewidth of 77 ps at 357 nm, and a corresponding 3-dB bandwidth of 780 MHz.
Acknowledgments
This work was supported by NATO Grant No. SfP971970, Turkish Department of Defense Grant No. KOBRA-002, and FUSAM-03.
