mos capacitors on epitaxial ge-si1-xgex with high-κ dielectrics using rpcvd

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1532 IEEE TRANSACTIONS ON ELECTRON DEVICES, VOL. 51, NO. 9, SEPTEMBER 2004 [12] I. C. Chen, S. Holland, and C. Hu, “A quantitative physical model for time-dependent breakdown in SiO ,” in Proc. IRPS, 1985, pp. 24–30. [13] D. J. DiMaria and J. H. Stathis, “Electron energy dependence of metal–oxide–semiconductor degradation,” Appl. Phys. Lett., vol. 75, no. 16, pp. 2427–2428, 1999. [14] P. E. Nicollian, W. R. Hunter, and J. C. Hu, “Experimental evidence for voltage driven breakdown models in ultrathin gate oxides,” in Proc. IRPS, 2000, pp. 7–15. [15] E. Wu, A. Vayshenker, E. Nowak, J. Sune, R.-P. Vollertsen, W. Lai, and D. Harmon, “Experimental evidence of power-law for voltage de- pendence of oxide breakdown in ultrathin gate oxides,” IEEE Trans. Electron Devices, vol. 49, pp. 2244–2253, Dec. 2002. [16] C. Leroux, P. Andreucci, and G. Reimbold, “Analysis of oxide break- down mechanism occurring during ESD pulses,” in Proc. Int. Rel. Phys. Symp., 2000, pp. 276–282. [17] G. Krieger, “Nonuniform ESD current distribution due to improper metal routing,” in Proc. EOS/ESD Symp., 1991, pp. 104–109. [18] S.-J. Wang, I.-C. Chen, and H. L. Tigelaar, “TDDB on poly-gate single doping type capacitors,” in Proc. IRPS, 1992, pp. 54–57. [19] E. Rosenbaum, J. C. King, and C. Hu, “Accelerated testing of SiO re- liability,” IEEE Trans. Electron Devices, vol. 43, pp. 70–80, Jan. 1996. [20] M. Alam, J. Bude, and A. Ghetti, “Field acceleration for oxide break- down—Can an accurate anode hole injection model resolve the E versus 1/E controversy?,” in Proc. IEEE. Int. Rel. Phys. Symp., 2000, pp. 21–26. [21] T. Nigam, R. Degraeve, G. Groeseneken, M. Heyns, and H. Maes, “A fast and simple methodology for lifetime prediction of ultrathin oxides,” in Proc. IEEE Int. Rel. Phys. Symp., 1999, pp. 381–388. [22] S. Voldman, private communication IBM. [23] T. Nigam, R. Degraeve, G. Groeseneken, M. Heyns, and H. Maes, “Con- stant current charge-to-breakdown: Still a valid tool to study the reli- ability of MOS structures?,” in IEEE Int. Rel. Phys. Symp., 1998, pp. 62–69. [24] Y. Shi, T. P. Ma, S. Prasad, and S. Dhanda, “Polarity-dependent tunneling current and oxide breakdown in dual-gate CMOSFETs,” IEEE Electron Device Lett., vol. 19, pp. 391–393, Oct. 1998. [25] ANSYS User’s Manual. [26] S. M. Lee and D. G. Cahill, “Heat transport in thin dielectric films,” J. Appl. Phys., vol. 81, no. 6, pp. 2590–2595, 1997. [27] D. Cahill, private communication. [28] S. Touloukian, R. W. Powell, C. Y. Ho, and P. G. Klemens, Thermophys- ical Properties of Matter. New York: IFI/Plenum, 1970, vol. 2. [29] MEDICI User’s Manual. [30] D. J. DiMaria and J. W. Stasiak, “Trap generation in silicon dioxide pro- duced by hot electrons,” J. Appl. Phys., vol. 65, pp. 2342–2350, 1989. [31] V. M. Dwyer, A. J. Franklin, and D. S. Campbell, “Thermal failure in semiconductor devices,” Solid State Electron., vol. 33, no. 5, pp. 553–560, 1990. [32] R. Moazzami, J. C. Lee, and C. Hu, “Temperature acceleration of time- dependent dielectric breakdown,” IEEE Trans. Electron Devices, vol. 36, pp. 2462–2465, Nov. 1989. [33] M. A. Alam, B. Weir, J. Bude, P. Silverman, and D. Monroe, “Explana- tion of soft and hard breakdown and its consequences for area scaling,” in IEDM Tech. Dig., 1999, pp. 449–452. [34] D. J. DiMaria, E. Cartier, and D. Arnold, “Impact ionization, trap cre- ation, degradation, and breakdown in silicon dioxide films on silicon,” J. Appl. Phys., vol. 73, no. 7, pp. 3367–3384, 1993. [35] K. F. Schuegraf and C. Hu, “Hole injection SiO breakdown model for very low voltage lifetime extrapolation,” IEEE Trans. Electron Devices, vol. 41, pp. 761–766, May 1994. [36] R. Degraeve, G. Groeseneken, R. Bellens, J. L. Ogier, M. Depas, P. J. Roussel, and H. E. Maes, “New insights in the relation between electron trap generation and the statistical properties of oxide breakdown,” IEEE Trans. Electron Devices, vol. 45, pp. 904–910, Apr. 1998. [37] D. J. DiMaria and E. Cartier, “Mechanism for stress-induced leakage currents in thin silicon dioxide films,” J. Appl. Phys., vol. 78, no. 6, pp. 3883–3894, 1995. [38] E. Rosenbaum and C. Hu, “High-frequency time-dependent breakdown of SiO2,” IEEE Electron Device Lett., vol. 12, p. 267, June 1991. [39] E. Rosenbaum, Z. Liu, and C. Hu, “Silicon dioxide breakdown lifetime enhancement under bipolar bias conditions,” IEEE Trans. Electron De- vices, vol. 40, p. 2287, Dec. 1993. [40] R. Tu, J. King, H. Shin, and C. Hu, “Simulating process-induced gate oxide damage in circuits,” IEEE Trans. Electron Devices, vol. 44, pp. 1393–1400, Sept. 1997. MOS Capacitors on Epitaxial Ge–Si Ge with High- Dielectrics Using RPCVD X. Chen, S. Joshi, J. Chen, T. Ngai, and S. K. Banerjee Abstract—We report the successful growth of MOS capacitor stacks with low temperature strained epitaxial Ge or Si Ge layer di- rectly on Si substrates, and with HfO EOT as high- di- electrics, both using a novel remote plasma-assisted chemical vapor de- position technique. These novel MOS capacitors, which were fabricated entirely at or below 400 C, exhibit normal capacitance–voltage and cur- rent–voltage characteristics. Index Terms—Ge-epi-on-Si, high- , MOS, remote plasma-assisted chemical vapor deposition (RPCVD). I. INTRODUCTION High- dielectrics on Ge have been recently studied in order to sig- nificantly reduce gate leakage while enhancing channel carrier trans- port in MOSFET application [1], [2]. However, these studies were on bulk Ge substrates, which have poor mechanical and thermal proper- ties, and high cost as compared to Si. Also, extra process complexity is involved in cleaning the unstable native oxide on Ge. Using a remote plasma-assisted chemical vapor deposition (RPCVD) system, we have recently demonstrated growth of the first MOS capacitor stacks with low-temperature strained epitaxial Ge or Si Ge layer di- rectly on Si substrates, and with HfO effective oxide thickness (EOT) as dielectric, both using our RPCVD system. The epitaxial Ge or Si Ge layer is of the order of the inversion layer thickness, which should effectively confine both electrons and holes in the inversion layer under a gate bias and is potentially beneficial for high-mobility channel MOSFET application. In this brief, we investi- gate both physical and electrical characteristics of the MOS capacitors. II. EXPERIMENTAL The MOS capacitors were fabricated on p-type silicon substrates, which had 50 to 70 Ge or Si Ge epitaxial layers deposited on them by RPCVD at 250 C to 300 C. Sample growth parameters are listed in Table I. During epitaxial layer deposition, plasma power, chamber pressure, substrate bias, GeH , SiH and Ar flows were modulated to control the interface and epitaxial quality. We then deposited 30 to 50 RPCVD HfO in another chamber in the RPCVD system at 250 C using a hafnium -butoxide precursor without oxygen flow. After the samples were unloaded from RPCVD system, subsequent processing steps include post-deposition annealing (400 C, 1 min, N ambient), TaN metal deposition using dc mag- netron sputtering, capacitor area patterning and reactive ion etching, and backside Al deposition and sintering (400 C, 10 min). The entire device fabrication was performed at or below 400 C. For comparison, MOS capacitors directly on Si substrate were also fabricated using the same procedure. Manuscript received September 17, 2003; revised April 27, 2004. This work was supported in part by the Semiconductor Research Corporation (SRC), in part by the MACRO Focus Center, the Micron Foundation, Texas Instruments, and in part by Applied Materials. The review of this brief was arranged by Editor G. Groeseneken. The authors are with the Microelectronics Research Center, The University of Texas at Austin, Austin, TX 78758 USA (e-mail: [email protected]). Digital Object Identifier 10.1109/TED.2004.833957 0018-9383/04$20.00 © 2004 IEEE

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1532 IEEE TRANSACTIONS ON ELECTRON DEVICES, VOL. 51, NO. 9, SEPTEMBER 2004

[12] I. C. Chen, S. Holland, and C. Hu, “A quantitative physical model fortime-dependent breakdown in SiO ,” in Proc. IRPS, 1985, pp. 24–30.

[13] D. J. DiMaria and J. H. Stathis, “Electron energy dependence ofmetal–oxide–semiconductor degradation,” Appl. Phys. Lett., vol. 75,no. 16, pp. 2427–2428, 1999.

[14] P. E. Nicollian, W. R. Hunter, and J. C. Hu, “Experimental evidencefor voltage driven breakdown models in ultrathin gate oxides,” in Proc.IRPS, 2000, pp. 7–15.

[15] E. Wu, A. Vayshenker, E. Nowak, J. Sune, R.-P. Vollertsen, W. Lai, andD. Harmon, “Experimental evidence of t power-law for voltage de-pendence of oxide breakdown in ultrathin gate oxides,” IEEE Trans.Electron Devices, vol. 49, pp. 2244–2253, Dec. 2002.

[16] C. Leroux, P. Andreucci, and G. Reimbold, “Analysis of oxide break-down mechanism occurring during ESD pulses,” in Proc. Int. Rel. Phys.Symp., 2000, pp. 276–282.

[17] G. Krieger, “Nonuniform ESD current distribution due to impropermetal routing,” in Proc. EOS/ESD Symp., 1991, pp. 104–109.

[18] S.-J. Wang, I.-C. Chen, and H. L. Tigelaar, “TDDB on poly-gate singledoping type capacitors,” in Proc. IRPS, 1992, pp. 54–57.

[19] E. Rosenbaum, J. C. King, and C. Hu, “Accelerated testing of SiO re-liability,” IEEE Trans. Electron Devices, vol. 43, pp. 70–80, Jan. 1996.

[20] M. Alam, J. Bude, and A. Ghetti, “Field acceleration for oxide break-down—Can an accurate anode hole injection model resolve the E versus1/E controversy?,” inProc. IEEE. Int. Rel. Phys. Symp., 2000, pp. 21–26.

[21] T. Nigam, R. Degraeve, G. Groeseneken, M. Heyns, and H. Maes, “Afast and simple methodology for lifetime prediction of ultrathin oxides,”in Proc. IEEE Int. Rel. Phys. Symp., 1999, pp. 381–388.

[22] S. Voldman, private communication IBM.[23] T. Nigam, R. Degraeve, G. Groeseneken, M. Heyns, and H. Maes, “Con-

stant current charge-to-breakdown: Still a valid tool to study the reli-ability of MOS structures?,” in IEEE Int. Rel. Phys. Symp., 1998, pp.62–69.

[24] Y. Shi, T. P. Ma, S. Prasad, and S. Dhanda, “Polarity-dependent tunnelingcurrent and oxide breakdown in dual-gate CMOSFETs,” IEEE ElectronDevice Lett., vol. 19, pp. 391–393, Oct. 1998.

[25] ANSYS User’s Manual.[26] S. M. Lee and D. G. Cahill, “Heat transport in thin dielectric films,” J.

Appl. Phys., vol. 81, no. 6, pp. 2590–2595, 1997.[27] D. Cahill, private communication.[28] S. Touloukian, R. W. Powell, C. Y. Ho, and P. G. Klemens, Thermophys-

ical Properties of Matter. New York: IFI/Plenum, 1970, vol. 2.[29] MEDICI User’s Manual.[30] D. J. DiMaria and J. W. Stasiak, “Trap generation in silicon dioxide pro-

duced by hot electrons,” J. Appl. Phys., vol. 65, pp. 2342–2350, 1989.[31] V. M. Dwyer, A. J. Franklin, and D. S. Campbell, “Thermal failure

in semiconductor devices,” Solid State Electron., vol. 33, no. 5, pp.553–560, 1990.

[32] R. Moazzami, J. C. Lee, and C. Hu, “Temperature acceleration of time-dependent dielectric breakdown,” IEEE Trans. ElectronDevices, vol. 36,pp. 2462–2465, Nov. 1989.

[33] M. A. Alam, B. Weir, J. Bude, P. Silverman, and D. Monroe, “Explana-tion of soft and hard breakdown and its consequences for area scaling,”in IEDM Tech. Dig., 1999, pp. 449–452.

[34] D. J. DiMaria, E. Cartier, and D. Arnold, “Impact ionization, trap cre-ation, degradation, and breakdown in silicon dioxide films on silicon,”J. Appl. Phys., vol. 73, no. 7, pp. 3367–3384, 1993.

[35] K. F. Schuegraf and C. Hu, “Hole injection SiO breakdown model forvery low voltage lifetime extrapolation,” IEEE Trans. Electron Devices,vol. 41, pp. 761–766, May 1994.

[36] R. Degraeve, G. Groeseneken, R. Bellens, J. L. Ogier, M. Depas, P. J.Roussel, and H. E. Maes, “New insights in the relation between electrontrap generation and the statistical properties of oxide breakdown,” IEEETrans. Electron Devices, vol. 45, pp. 904–910, Apr. 1998.

[37] D. J. DiMaria and E. Cartier, “Mechanism for stress-induced leakagecurrents in thin silicon dioxide films,” J. Appl. Phys., vol. 78, no. 6, pp.3883–3894, 1995.

[38] E. Rosenbaum and C. Hu, “High-frequency time-dependent breakdownof SiO2,” IEEE Electron Device Lett., vol. 12, p. 267, June 1991.

[39] E. Rosenbaum, Z. Liu, and C. Hu, “Silicon dioxide breakdown lifetimeenhancement under bipolar bias conditions,” IEEE Trans. Electron De-vices, vol. 40, p. 2287, Dec. 1993.

[40] R. Tu, J. King, H. Shin, and C. Hu, “Simulating process-induced gateoxide damage in circuits,” IEEE Trans. Electron Devices, vol. 44, pp.1393–1400, Sept. 1997.

MOS Capacitors on Epitaxial Ge–Si Ge withHigh- Dielectrics Using RPCVD

X. Chen, S. Joshi, J. Chen, T. Ngai, and S. K. Banerjee

Abstract—We report the successful growth of MOS capacitor stacks withlow temperature strained epitaxial Ge or Si Ge ( = 0 9) layer di-rectly on Si substrates, and with HfO (EOT = 9 7 �A) as high- di-electrics, both using a novel remote plasma-assisted chemical vapor de-position technique. These novel MOS capacitors, which were fabricatedentirely at or below 400 C, exhibit normal capacitance–voltage and cur-rent–voltage characteristics.

Index Terms—Ge-epi-on-Si, high- , MOS, remote plasma-assistedchemical vapor deposition (RPCVD).

I. INTRODUCTION

High-� dielectrics on Ge have been recently studied in order to sig-nificantly reduce gate leakage while enhancing channel carrier trans-port in MOSFET application [1], [2]. However, these studies were onbulk Ge substrates, which have poor mechanical and thermal proper-ties, and high cost as compared to Si. Also, extra process complexity isinvolved in cleaning the unstable native oxide on Ge. Using a remoteplasma-assisted chemical vapor deposition (RPCVD) system, we haverecently demonstrated growth of the first MOS capacitor stacks withlow-temperature strained epitaxial Ge or Si1�x Gex(x = 0:9) layer di-rectly on Si substrates, and with HfO2 effective oxide thickness (EOT)= 9:7 �A as dielectric, both using our RPCVD system. The epitaxialGe or Si1�x Gex(x > 0:9) layer is of the order of the inversion layerthickness, which should effectively confine both electrons and holes inthe inversion layer under a gate bias and is potentially beneficial forhigh-mobility channel MOSFET application. In this brief, we investi-gate both physical and electrical characteristics of the MOS capacitors.

II. EXPERIMENTAL

The MOS capacitors were fabricated on p-type silicon substrates,which had 50 to 70 �A Ge or Si1�xGex(x = 0:9) epitaxial layersdeposited on them by RPCVD at 250 �C to 300 �C. Sample growthparameters are listed in Table I. During epitaxial layer deposition,plasma power, chamber pressure, substrate bias, GeH4, SiH4 and Arflows were modulated to control the interface and epitaxial quality.We then deposited 30 to 50 �A RPCVD HfO2 in another chamber inthe RPCVD system at 250 �C using a hafnium t-butoxide precursorwithout oxygen flow. After the samples were unloaded from RPCVDsystem, subsequent processing steps include post-deposition annealing(400 �C, 1 min, N2 ambient), TaN metal deposition using dc mag-netron sputtering, capacitor area patterning and reactive ion etching,and backside Al deposition and sintering (400 �C, 10 min). The entiredevice fabrication was performed at or below 400 �C. For comparison,MOS capacitors directly on Si substrate were also fabricated using thesame procedure.

Manuscript received September 17, 2003; revised April 27, 2004. This workwas supported in part by the Semiconductor Research Corporation (SRC), inpart by the MACRO Focus Center, the Micron Foundation, Texas Instruments,and in part by Applied Materials. The review of this brief was arranged by EditorG. Groeseneken.

The authors are with the Microelectronics Research Center, The Universityof Texas at Austin, Austin, TX 78758 USA (e-mail: [email protected]).

Digital Object Identifier 10.1109/TED.2004.833957

0018-9383/04$20.00 © 2004 IEEE

IEEE TRANSACTIONS ON ELECTRON DEVICES, VOL. 51, NO. 9, SEPTEMBER 2004 1533

TABLE ISAMPLE GROWTH PARAMETERS

Fig. 1. High-resolution TEM image of TaN–HfO –Ge-epitaxy–Si-substratestack.

III. RESULTS AND DISCUSSION

The strained Ge and Si1�xGex epitaxial layers were confirmedby cross-sectional high resolution transmission electron microscopy(HRTEM) analysis as shown in Fig. 1. X-ray differential (XRD)characterization of the thin films was attempted but the measurementresults could not be matched satisfactorily to the simulation resultsdue to noise dominated measurement and difficult modeling of thinstrained films. HRTEM on thin bare Ge films and films cappedwith only the thin dielectric are difficult as the films can be easilydamaged due to the sample preparation procedure. Hence we choseto prepare transmission electron microscopy (TEM) samples withthe gate metal deposited on the gate dielectric. Owing to the lowtemperature metastable RPCVD growth, high–quality 65 �A epitaxialGe layer is achieved (Fig. 1), which is well beyond the predictedequilibrium critical layer thickness (CLT) (< 10 �A)). The threadingdislocation density was estimated to be less than 107–cm2 by countingline defects per unit area on plan view TEM images (not shown). TheRMS roughness for Ge and Si1�xGex epitaxial layers as determinedby atomic force microscopy is 1.4–1.5 �A, indicating a smooth surfacefor subsequent HfO2 growth. Smooth HfO2 deposition was achievedon both epitaxial Ge and Si, as shown in Figs. 1 and 2. Notice thatthe interfacial layer is � 10 �A on Si, but is less than 5-�A on a Geepitaxial layer presumably because Ge oxides tend to be volatile at ahigh temperature and under a high vacuum. We have compared (HfO2

deposition at 250 �C with and without plasma. X-ray photon spec-troscopy (XPS) analysis (Fig. 3) shows an Hf metal peak at 15 eV fordeposition without plasma, indicating an incomplete (HfO2 reaction.Also, the growth rate for RPCVD (HfO2 (70 �A=min) was found to betwice as that without a plasma. Hence, RPCVD is a feasible processfor low-temperature, (< 300 �C) high-� material growth.

Fig. 2. High-resolution TEM image of TaN–HfO (IL)–Si-substrate stack.

Fig. 3. XPS analysis of HfO films deposited with (solid line) and withoutplasma (dotted line). A Hf metal peak is observed for deposition without plasma.

The resulting MOS capacitors exhibit normal C–V characteristics,as illustrated in Fig. 4(a)–(c). The low-frequency curves (dotted lines)were calculated from the measured high-frequency capacitance withQM correction, indicating good agreement in accumulation and deple-tion regions and reasonable agreement in the inversion region. The ca-pacitors with Ge and SiGe layers show a flat band voltage shift as com-pared to the control samples which can be attributed to the worse inter-facial quality and even inter diffusion between the layers and the dielec-tric due to inferior oxides of these layers. The values of capacitance andleakage scale linearly with capacitor sizes indicating negligible edgeeffects. Equivalent oxide thickness (EOT) of (HfO2 on Ge is deter-mined to be 9.7 �A, which is significantly less than that on Si (20 �A),due to the lower interfacial thickness between (HfO2 and Ge. The ef-fective dielectric constant is 10–14. If the contribution of interfaciallayer is accounted for, the dielectric constant of HfO2 is 16–24, whichmakes RPCVD (HfO2 a very promising gate dielectric. The interfacestate density (Dit), extracted using the CVC program from NCSU 1 onHfO2–Si stack is � 1011–cm2, which is comparable to currently re-ported values [3]. TheDit on (HfO2–Ge–Si and (HfO2–Si1�xGex–Sistacks are of the order of 1012–cm2, probably due to the less stable in-terface characteristics between HfO2 and Ge or Si1�xGex layers. Thehigher values of the Dit are reflected in the slightly higher stretch outin the capacitance–voltage (C–V) of the samples with the Ge and SiGelayers. Leakage currents densities of these thin (HfO2 films at �1 Vare � 10�2 A/cm�2 with reasonably well behaved J–V characteris-tics (Fig. 5). These values are comparable with recent values with sim-ilar EOTs for gate stacks of (HfO2 on Si [4], [5], and are three ordersof magnitude lower than that of other reported HfO2 on Ge for sim-ilar EOTs [1]. We have attributed this significant leakage reduction toour capability of growing both epitaxial Ge layer and high-� dielectric

1CVC is a Program Developed by Dr. Hauser/N C State University.

1534 IEEE TRANSACTIONS ON ELECTRON DEVICES, VOL. 51, NO. 9, SEPTEMBER 2004

Fig. 4. (a) Measured and simulated C–V characteristics of TaN–HfO –Sistack (Dit = 1:5 e cm EOT =20 �A) (b) Measuredand simulated C–V characteristics of TaN–HfO –Ge–Si stack(Dit = 3:7 e cm EOT =9:7 �A) (c) Measured andsimulated C–V characteristics of TaN–HfO –Si Ge –Si stack(Dit = 1:4 e cm EOT =14:5 �A)D and EOT values were extractedfrom the high frequency C–V curve. We used the CVC program by Dr. Hauserfrom NCSU.

layer in the same RPCVD system, thus avoiding possible interfacialcontamination effects. Even though these leakage current densities arelow, they are still not low enough to perform low frequency C–V mea-surements without being dominated by leakage current, especially onthe capacitors with the Ge and SiGe layers where the interface is un-stable.

In summary, we have demonstrated the successful low tempera-ture growth of MOS capacitor stacks with strained epitaxial Ge orSi1�xGex(x = 0:9) layer directly on Si substrates, and with HfO2

(EOT = 9:7 �A) as high-� dielectrics, both using a novel RPCVDtechnique. These well-behaved MOS capacitors showed that theRPCVD process is a very promising technique for low thermal budgetand high device performance applications.

REFERENCES

[1] C. Chui, S. Ramanathan, B. B. Triplett, P. C. McIntyre, and K. C.Saraswat, Proc. IEEE Device Research Conf., 2002, pp. 191–192.

Fig. 5. J–V characteristics of RPCVD HfO2on different stacks. The leakagecurrent is 10�2 A/cm2at�1 Vfor (HfO2(EOT � 9:7 �A)–Ge–Si stack.

[2] C. Chui, H. Kim, D. Chi, B. B. Triplett, P. C. McIntyre, and K. C.Saraswat, IEDM Tech. Dig., 2002, pp. 437–440.

[3] L. Kang, B. H. Lee, W. Qi, Y. Jeon, R. Nieh, S. Gopalan, K. Onishi, andJ. C. Lee, IEEE Electron Device Lett., vol. 21, pp. 181–183, Feb., 2000.

[4] S. J. Lee, T. S. Jeon, D. L. Kwong, and R. Clark, J. Appl. Phys., vol. 92,no. 5, pp. 2807–2809, 2002.

[5] P. D. Kirsch, C. S. Kang, J. Lozano, J. C. Lee, and J. G. Ekerdt, J. Appl.Phys., vol. 91, no. 7, pp. 4353–4363, 2002.

Effects of Spacer Thickness on Noise Performance ofBipolar Transistors

Wai-Kit Lee, Sang Lam, and Mansun Chan

Abstract—The effects of spacer thickness on noise performance of abipolar junction transistor with different emitter widths and operationfrequencies are examined. The minimum noise figure ( ) derivedfrom the -parameters as well as the base ( ) and emitter resistance( ) obtained from the device simulation is used as a measure of noisecharacteristics. Furthermore, the noise resistance ( ), optimum sourceadmittance ( ), and the associated gain ( ) are also given inthis brief. To achieve the minimum value of , the spacer thicknessshould be targeted to an optimal value, and its value is frequency andgeometry dependent.

Index Terms—Bipolar transistors, modeling, SiGe heterojunctionbipolar transistors, spacer thickness.

I. INTRODUCTION

Base resistance plays an important role in determining the noiseperformance of a bipolar junction transistor (BJT) device. When theemitter width is scaled down, the spacer thickness becomes more im-portant in determining the overall base resistance. Although reducing

Manuscript received April 19, 2004; revised June 22, 2004. This work wassupported by the Research Grant Council of Hong Kong under Grant HKUST6207/02E. The review of this brief was arranged by Editor M. J. Deen.

The authors are with the Department of Electrical and Electronic Engineering,Hong Kong University of Science and Technology, Clear Water Bay, Kowloon,Hong Kong.

Digital Object Identifier 10.1109/TED.2004.833959

0018-9383/04$20.00 © 2004 IEEE