1 Introduction

The wide bandgap semiconductors GaN and SiC hold great promise for high temperature and high power electronics. This is due to their attractive material properties, such as high breakdown fields, high thermal conductivities, high saturated electron velocities, and adequate electron mobilities. [a] [3] [4] By growing GaN directly on SiC one can make n-p heterojunctions. [5], [6] Adding a SiC collector layer led to the demonstration of high temperature and high power GaN/6H-SiC HBTs. [7], [8] These transistors exhibited an extraordinarily high room temperature current gain of >106 and were able to operate at 535° C with a gain of 100. However, in more recent work this performance could not easily be reproduced due to the presence of a deep defect level in the p-type 6H-SiC. [9] The possibility of obtaining higher quality 4H-SiC than 6H-SiC seemed appealing due to the larger bandgap energy and superior electron mobility (especially along the C-axis). In this paper, we report on GaN/SiC HBTs using the 4H polytype.

2 Device design

There are several design issues worth mentioning. Making HBTs from GaN/4H-SiC instead of using GaN/6H-SiC reduces the expected current gain (β), because the emitter injection efficiency (γE) has a strong dependence on the difference in the bandgap energies (ΔEg) as shown in Equation (1). [10]

$$ {{\gamma _E} = \frac{1}{{1 + \frac{{{I_{p,E}}}}{{{I_{n,E}}}}{\text{and}}}}} \\ {\frac{{{I_{p,E}}}}{{{I_{n,E}}}} = \frac{{{x_B}{D_{p,E}}{N_B}}}{{{L_{p,E}}{D_{n,B}}{N_E}}}\frac{{{N_{c,E}}{N_{v,E}}}}{{{N_{c,B}}{N_{v,B}}}}{{\text{e}}^{\frac{{\Delta E}}{{kT}}}}} \\ $$
((1))

where Ip,E and In,E are the emitter hole and electron currents, Lp,E is the hole diffusion length in the emitter, xB is the quasi-neutral base width, NE and NB are the doping densities in the emitter and base, DE and DB are the diffusion constants in the emitter and the base, and Nc and Nv are the effective density of states at the conduction and valence band-edges, respectively. Although ΔEg is smaller for GaN/4H-SiC at 0.2 eV than for GaN/ 6H-SiC at 0.4 eV, the theoretical current gain can still be large for well-designed HBTs. First order calculations, using an electron mobility in the base of 100 cm2/V-s and a minority carrier life time in the base of 10 ns, indicate that the current gain is limited by the base transport to 128. The emitter efficiency was calculated at 0.9997 so that the device is not expected to be limited by the hole injection into the emitter. Furthermore, the large ΔEg allows the p-SiC base to be heavily doped, which decreases the base resistance and the sensitivity to the Early effect without compromising the emitter efficiency (see Equation (1)). The heavily doped base is also practical for making tunneling contacts to the p-type SiC. [11]

Recently, an AlGaN/GaN HBT was demonstrated with a dc current gain of 3 at room temperature. [12] However, our hybrid GaN/SiC approach with an indirect bandgap p-SiC base has an intrinsic advantage over a direct bandgap p-GaN base. This is because the minority carrier lifetime is much longer in SiC compared to GaN, which means a higher base transport factor. Furthermore, by using commercially available p-SiC one avoids the current material difficulties associated with p-GaN. [12] Admittedly, growing GaN/SiC junctions with good electrical characteristics is probably more challenging than in the AlGaN/GaN materials system. The growth is especially important since great care must be taken to minimize minority carrier recombination at the emitter-base heterojunction to obtain high emitter injection efficiency. [13]

3 Device Fabrication

A cross sectional schematic of the GaN/SiC HBT structure is shown in Figure 1.

Figure 1
figure 1

A cross section of two adjacent GaN/SiC HBTs.

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The SiC epi-layers used in this study were grown by MOCVD on commercial 4H-SiC Si-face (n~1018 cm−3) substrates. The SiC part of the HBT consists of a 1-μm-thick n-type (5×1017cm−3) SiC collector with a 0.225-μm-thick p-type base layer. The p-type doping concentration (Al) is Na=5×1019 cm−3, but the hole concentration was not measured in these samples. Device isolation was provided by reactive ion etching (RIE) to form a trench around each device. RIE was performed with Freon 14 (CF4) at 35mT with a 20 sccm gas flow rate at a power density of 0.14 W/cm2 (100W in our system). A 70-nm-thick SiO2 layer was then grown by thermal wet oxidation at 1175° C. This SiO2 layer provides collector-base junction passivation in addition to serving as a mask for selective area GaN growth. [14] The emitter patterns are transferred to the SiO2 using standard photolithography and an HF etch. Next, the GaN emitter was grown by MOCVD. [13] The emitters are typically ~0.5-μm-thick and unintentionally doped. Note that low-temperature GaN or AlN nucleation (buffer) layers were not used. An SEM picture exhibiting a selectively grown GaN emitter finger is shown in Figure 2.

Figure 2
figure 2

An SEM picture of a GaN emitter finger grown on patterned SiO2/p-SiC/n-SiC using MOCVD.

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Ti/Au and Al/Ti/Au contacts were formed to the n-GaN emitter and the p-SiC base, respectively, using the standard photoresist lift-off technique. A Ni/Au bi-layer was used as a large area n-SiC back contact. Pictures of two completed devices are shown in Figure 3.

Figure 3
figure 3

Pictures of two completed GaN/SiC HBT structures with one GaN emitter finger (left) and four GaN emitter fingers (right). The emitter widths in both devices are 10 μm.

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Current-voltage (I-V) measurements were performed using a probe station and an HP4145B semiconductor parameter analyzer. The high temperature measurements were made using a copper sample holder heated by a hotplate. Convection cooling was avoided by enclosing the copper block and sample in a metal container covered by glass microscope slides with holes for the probe tips. The temperature was measured using a thermocouple that was calibrated using Timpilsticks® and by melting various metals.

4 Results and Discussion

Typical room temperature common base I-V characteristics for the GaN/4H-SiC HBTs are shown in Figure 4. This particular device had one 10μm x 100μm emitter finger as shown in Figure 3 (left).

Figure 4
figure 4

Room temperature common base I-V characteristics for a GaN/4H-SiC HBT. The emitter current is stepped in 1mA increments from 1mA.

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The emitter current was stepped at 1mA increments. The saturated collector current is nearly equal to the emitter current, with a maximum dc current gain (β=Ic/IB) of 15 at room temperature. The onset of collector current is slightly above -3V, which corresponds roughly to the built-in potential in the 4H-SiC (Eg=3.2 eV) collector-base p-n junction at these doping levels. Breakdown in these devices occurs above 15V. As expected, due to the heavily doped base, the Early voltage is too large to measure accurately. Common emitter operation was not obtained in these HBTs, probably due to the large voltage dependent leakage current in the collector-base junction. Next, we will discuss the electrical characteristics of the individual collector-base and emitter-base pn junctions.

Typical room temperature I-V characteristics for the base-emitter heterojunction (broken line) and the base-collector junction (solid line) are shown in Figure 5.

Figure 5
figure 5

Room temperature I-V characteristics for the base-emitter heterojunction (broken line) and the base-collector junction (solid line).

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The collector-base junction exhibits significant reverse leakage and forward recombination or tunneling currents. However, there is a kink in the I-V trace at about +3V volts indicating the presence of forward injection current. No meaningful ideality factor or saturation current was extracted. Similar conclusions can be drawn for the emitter-base heterojunction. The voltage dependent reverse leakage current is significant, and the forward current onset voltage is too low for a pn junction with a built in potential of ~3 V indicating recombination or tunneling. Both tunneling and recombination are loss mechanisms that would explain the low gain in these HBTs.

Gummel plots for the HBTs measured at room temperature and at 300° C are shown in Figure 6 and Figure 7, respectively.

Figure 6
figure 6

Gummel plot measured at room temperature from an HBT with one GaN emitter finger (A = 10×100μm2).

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Figure 7
figure 7

Gummel plot measured at 300° C.

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Note that there is significant leakage current present at low emitter-base voltages (lower than the built-in potential). However, this was also observed in the early GaN/6H-SiC HBTs, which had leaky collector-base junctions. More ideal Gummel plots were obtained by improving the electrical characteristics in the collector-base junctions. [15] At high VBE the current is dominated by series resistance. Even so, the devices exhibit a dc current gain of 15 at room temperature and 3 at 300°C. The current gain was measured at VBE = 5V. It is worth noting that by removing the base contact no collector current was observed eliminating the possibility of a short through the device. In other words, a small base current is required for transistor operation.

The dc current gain at VBE=5V was measured as a function of temperature and plotted in an Arrhenius fashion as shown in Figure 8.

Figure 8
figure 8

Arrhenius plot of the dc current gain measured at Vbe=5V. The extracted activation energy is 0.07 eV.

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The current gain decreases with increasing temperature, and the extracted activation energy is 0.07 eV. However, the temperature dependence of the gain indicates that the gain is not limited by the emitter efficiency, as a much larger gain and a larger temperature dependence (Ea = ΔEg = 0.2 eV) would be expected. Instead it can be explained by the temperature variation of the mobility, which leads to a temperature variation of the diffusion constant and transit time in the base.

Assuming uniform current injection across the (10 × 100 μm2) emitter-base junction results in a maximum current density of 500A/cm2 at 15V. The corresponding power density is therefore 7.5 kW/cm2.

5 Conclusions

We have demonstrated the first 4H-SiC/GaN HBT structure and have successfully operated the device between room temperature and 300°C. The devices could sustain a maximum current density of 500 A/cm2 at power density of 7.5kW/cm2. The devices have some obvious deficiencies including large leakage currents and series resistances. Nevertheless we were able to demonstrate transistor action in those devices, which implies that there is no significant barrier for electrons flowing from the emitter into the base. 6H-SiC/GaN HBTs have been reported in the past with much larger current gain. Despite the lower gain of the 4H-SiC/GaN, we believe these devices to be distinctly superior to 6H-SiC/GaN device because of the higher electron mobility along the C-axis and the smaller temperature dependence of the current gain. These properties will lead to a larger transit frequency and operation over a wider temperature range in a microwave circuit.

Next, we need to improve the base (p-SiC) contacts and reduce the n-SiC collector doping density. Furthermore, a reduction of the leakage current in the large area base-collector junction, and a reduction of the recombination/tunneling current in the emitter base heterojunc-tion is expected to facilitate improved transistor characteristics and common emitter operation.