Degradation Study of AIGaN/GaN HEMT through Electro-Thermo-Mechanical Calculations and Thermo-Reflectance Measurements by MA SSAcHUSETTS INSTITUTE OF TECHNOLOGY Feng Gao NOV 19 2010 B.S., Physics (2008) LIBRARIES Fudan University Submitted to the Department of Materials Science and Engineering in Partial Fulfillment of the Requirements for the Degree of Master of Science in Materials Science and Engineering at the ARCHIVES Massachusetts Institute of Technology August 2010 @2010 Massachusetts Institute of Technology All rights reserved r Author U Department of Materials Science and Engineering August 13, 2010 Certified by Tomes Palacios Associate Professor of Electrical Engineering Thesis Supervisor And ' ari V. Thompson Professor of Materials Science and Engineering Thejsis ader Accepted by unnstopher Schuh Chair, Departmental Committee on Graduate Students Acknowledgment First of all, I would like to express my deepest gratitude to my thesis advisor, Prof. Tomas Palacios. He is one of the most energetic, smartest and kindest people I have ever known. It is my great fortune to join his group and be his student. During these two years, I learned a lot from him not only the knowledge of my research but also the characteristics of being a successful person. I always remember his encouragement when I got frustrated, 'You came to MIT to be the world expert in research. You have the greatest potential to provide the best work!' Had it not been his great guidance to my research and considerable support to my life, I would have never finished this thesis. Secondly, I would like to thank all my labmates: Bin Lu, Omari Saadat, Han Wang, Will Chung, Allen Hsu, Mohamed Azize, Kevin Ryu, Daniel Piedra and Benjamin Mailly for all the help and advice to my research. They are always good resource for ideas and discussions. In addition, I would like to thank my collaborator Katey Lo in Prof. Rajeev Ram's group for all her great help in my experiment setup and measurements. I also like to thank my thesis reader, Prof. Carl Thompson for giving me invaluable advice and suggestive comments in my thesis. Last but not least, I would like to share this thesis with my parents. Without their warming support and encouragement, I can hardly make it done. I love you from the bottom of my heart. This work was made possible by the DRIFT MURI project by the Office of Naval Research and by the National Reconnaissance Office. Degradation Study of AIGaN/GaN HEMT through Electro-Thermo-Mechanical Calculations and Thermo-Reflectance Measurements by Feng Gao Abstract During the last few years, AIGaN/GaN high electron mobility transistors (HEMTs) have been intensively studied for high frequency high power applications. In spite of this great interest, device reliability is still an important challenge for the wide deployment of AIGaN/GaN HEMT technology. To fully understand reliability in these devices, it is necessary to consider the electrical, mechanical and thermal properties of the operating AIGaN/GaN transistors. Since AIGaN and GaN are both piezoelectric materials, the coupling among electric field, lattice heating and mechanical characteristics gives rise to large changes in strain field and elastic energy density in the transistors under the pinch-off conditions. Most previous work have studied the inverse piezoelectric effect on device degradations, however, quantitative analysis of this failure mechanism is still needed. In this thesis, we have developed the first fullycoupled electro-thermo-mechanical simulation of AIGaN/GaN HEMTs to study the correlation between the critical voltages of the gate current degradation and the lattice temperature distributions of these devices under the reverse-gate-bias reliability testing. In addition, we have compared the numerical results of our simulations with DC measurements and high resolution thermo-reflectance images, obtaining excellent agreement for both of them. Moreover, our studies suggest a covenient and low-cost way to obtain the reliability characteristics of AIGaN/GaN HEMTs by using the thermo-reflectance measurements of the lattice temperature distributions for those devices. Content 5 CHAPTER 1 INTRODUCTIO N ....................................................................................................................................... 1.2 BACKGROUND AND M OTIVATION OF RELIABILITY STUDIES ............................................................................ 5 7 1.3 THESIS OUTLINES ........................................................................................................------............... 9 1.1 INTRODUCTION OFALGAN/GAN HEM Ts............................................................................................ 11 CHAPTER 2 SELF-CONSISTENT ELECTRO-THERMAL SIMULATIONS........................................................... 2.1 INTRODUCTION ..............................................................................................................................--- 11 2.2 BASIC SEMICONDUCTOR PHYSICS .......................................................................................................... 11 2.2.1 2.2.2 2.3 11 Poisson's Equation ............................................................................................................................. Carrier Continuity Equations..............................................................................................................12 12 DRIFT-DIFFUSION M ODEL.................................................................................................................... 2.3.1 Drift-Diffusion Transport Equations ............................................................................................... 2.4 LATTICE HEATING M ODEL .................................................................................................................... 2.4.1 Lattice Heat Flow Equation ................................................................................................................ 2.4.2 M odified Drift-Diffusion Equations ............................................................................................... 2.4.3 Heat Generation Equations................................................................................................................15 2.4.4 Therm al Boundary Conditions ........................................................................................................ 2.5 13 14 14 15 16 17 M OBILITY M ODEL .............................................................................................................................. 2.5.1 Low Field M obility M odel of AIGaN/GaN HEIMTs ........................................................................... 18 2.5.2 High Field M obility M odel of AIGaN/GaN HEM Ts................................................................... 19 2.6 20 SIMULATION RESULTS ......................................................................................................................... 2.6.1 Transistors Structures ........................................................................................................................ 2.6.2 IVCurves.............................................................................................................................................21 2.6.3 Electric Field Distribution ................................................................................................................... 2.6.4 Lattice Tem perature Distribution.................................................................................................. 2.7 SUMMARY ........................................................................................................................................ CHAPTER 3 THERM O-REFLECTANCE M EASUREM ENTS................................................................................ 21 22 25 26 27 27 3.1 INTRODUCTION .................................................................................................................................. 3.2 THEORY..................................................................................................................................--.- 3.3 EXPERIMENTAL SETUP ......................................................................................................................... 28 3.4 EXPERIMENTAL RESULTS...................................................................................................................... 29 .. 27 3.4.1 Calibration of Thermo-Reflectance Coefficient.............................................................................. 3.4.2 Lattice Tem perature Distribution .................................................................................................. 3.4.3 Experim ent vs. Sim ulation .................................................................................................................. 3.5 DISCUSSION ................................................................................................................................-----3.6 SUMMARY ........................................................................................................................---..---..---- 29 31 38 40 41 CHAPTER 4 PIEZOELECTRIC-THERM AL CALCULATIONS................................................................................. 42 4.1 INTRODUCTION .................................................................................................................................. 42 4.2 42 THEORY............................................................................................................................................ 3 4.2.1 4.2.2 4.2.3 4.2.4 4.2.5 4.2.6 4.2.7 4.2.8 4.3 CALCULATION RESULTS........................................................................................................................ 4.3.1 4.3 .2 4.3.3 4.4 Fundam ental Equation.......................................................................................................................42 Equati ons of State .............................................................................................................................. Alternative Form ulation ..................................................................................................................... M aterial Properties ............................................................................................................................ Constitutive Relations ........................................................................................................................ Equilibrium Equations ........................................................................................................................ The Boundary Conditions Problem ............................................................................................... Elastic Energy Density ........................................................................................................................ Strain .................................................................................................................................................. Stress .................................................................................................................................................. Elastic Energy Density ........................................................................................................................ SUMMARY ........................................................................................................................................ CHAPTER 5 REVERSE-GATE-BIAS RELIABILITY TESTING ................................................................................. 43 44 45 48 53 54 55 57 57 60 62 63 64 5.1 INTRODUCTION .................................................................................................................................. 64 5.2 STRUCTURE OF TESTED TRANSISTORS ................................................................................................... 64 5.3 CALIBRATION OF THERMO-REFLECTANCE COEFFICIENT .............................................................................. 65 5.4 DC M EASUREMENTS OF GATE CURRENT DEGRADATION ......................................................................... 65 5.5 THERMO-REFLECTANCE M EASUREMENTS OF DEGRADATION....................................................................... 67 5.6 DISCUSSION ...................................................................................................................................... 70 SUMMARY ........................................................................................................................................ 72 5.7 CHAPTER 6 CONCLUSIONS AND FUTURE W ORK ................................................................................................ 73 6.1 CONCLUSIONS ................................................................................................................................... 73 6.2 FUTURE W ORK .................................................................................................................................. 74 REFERENCE ................................................................................................................................................................... 75 .................................................... .. .... .... ............ .. ... .. ..... I.. ................................... ....... INTRODUCTION CHAPTER 1 1.1 Introduction of AlGaN/GaN HEMTs GaN-based high electron mobility transistors (HEMTs) have thrived since their first demonstration in 1993 [1]. In less than 20 years, they have evolved from devices with less than 20 mA/mm of output current and virtually no high-frequency performance, to devices with extremely high output power 900W at 2.9GHz and 81W at 9.5GHz, high frequency fT = 225 GHz at Lg = 60nm, high-power efficiency PAE = 75% at Psat = 100W, broadband operation 1.02.5 GHz with 50% efficiency [2] and world-wide commercialization since 2004 [3-6]. The great development and extraordinary performance of GaN-based HEMTs is mainly because of the outstanding electronic properties of AIGaN/GaN structures. Characteristic ________________ Bandgjap (eV) Electron Mobility at 300K (cm2! Vs) Saturated (peak) Electron Velocity (x10 7 cm/s) Critical Breakdown Field Silicon IInGaAs AIGaAs/ IlnGaAsI nAlAs/ 1.1 1.42 ,., 1.35 , , (W/cm-K) 3.266 1500 8500 5400 700 1500- 1.0 (1.0) 0.3 1.3 (2.1) 0.4 1.0 (2.3) 0.5 2.0 (2.0) 1.3 (2.1) 3.0 3.0 1.5 0.5 0.7 4.5 >1.5 (MV/cm) Thermal Conductivity SiC 15..75. Table 1.1 As shown in the Table 1.1, AIGaN/GaN structure has high electron mobility (>1500 cm 2N*s at room temperature) and high electron velocity (-2.5x1 0 7cm/s peak velocity and -1.3x10 7cm/s saturated velocity). In addition, strong piezoelectric and spontaneous polarization in Ill-nitride materials results in a high sheet carrier density (normally 0.7-1.4*1013 cm-2) in AIGaN/GaN hetero-structure without any conventional doping. The high electron mobility and carrier .... ............... ......... ... I-I.I..-.....,-,",--"",-,-,-,1--l'I",,-"",- - - - - _.' -- *'** - - - hetero-structure without any conventional doping. The high electron mobility and carrier concentration of AIGaN/GaN HEMTs allow the fabrication of these devices with maximum drain current densities in excess of 2 A/mm [7]. On the other hand, as a result of the wide band-gap (-3.49 eV) and high breakdown electric field (>3 MV/cm) of AIGaN/GaN structure, GaN-based HEMTs have very large breakdown voltage (8300V in [8]). Both high current density and large breakdown voltage are important requirements for power amplifiers. Moreover, the high electron velocity makes this material system one of the best candidates for very high frequency operation. *Miary 100 10 aN s 0.1 2 GHz 10 GHz 30 GHz 60 GHz Frequency Band Figure 1.1-1: Important potential applications for GaN-based power transistors Figure 1.1 summarizes some of the multiple commercial and military applications that could benefit from the use of AIGaN/GaN HEMTs as power devices. As shown above, these transistors can be used in many applications requiring high frequency and high power operations. At lower frequencies, AIGaN/GaN HEMTs are being pursued for power-switching applications [9] and even for biological [10] and chemical/physical sensors [11]. At higher frequencies, the performance of AIGaN/GaN HEMTs has been evolving very fast over the last 20 years. A maximum current gain cut-off frequency (fT) of 163 GHz was reported in AIGaN/GaN HEMTs with a gate length in the 60-90 nm range [12]. When biased for maximum __ power gain, these devices could reach 230 GHz of maximum power gain cut-off frequency (fmax) [13]. The last 20 years has also witnessed the great progress of the output power and power added efficiency (PAE) in GaN devices as power amplifiers. Currently, AIGaN/GaN HEMTs have been already commercially available for power amplification in cell-phone base stations at 2GHz and a total output power in excess of 280W have been reported at that frequency [14]. At 4GHz, AIGaN/GaN HEMTs have demonstrated more than 32 W mm' of output power with a PAE of 54.8% at Vds=120V [15]. This performance is more than one order of magnitude better than those of any other competing semiconductor technology such GaAs and InP. 1.2 Background and Motivation of Reliability Studies While GaN-based HEMTs are routinely presenting excellent performance, the greatest challenge for the wide deployment has been, and remains, achieving a high level of reliability and stability concurrently with high-performance operation [16]. First of all, improvements in reliability require a better understanding of the failure mechanisms of GaN-based HEMTs. Years of research into this area have identified the following major degradation modes, which can represent the peculiarities of the physics of GaN devices, the imperfection of the materials and the stability of the fabrication processes: " Schottky and Ohmic Contacts Degradation * Surface Trapping-induced Degradation * Hot Electron-induced Degradation * Inverse Piezoelectric-induced Degradation These four failure modes are also schematically demonstrated in a cross section of a typical AIGaN/GaN HEMT in the figure below, identifying critical areas which can be subjected to the degradation. .........-. ......... ........ Schottky Contacts Degradation Surface Trapping-induce Degradation Ohmic Contacts Degradation Hot Electron-induced Degradation Inverse Piezoelectricinduced Degradation Figure 1.2-1: Schematic cross section of an AIGaN/GaN HEMT. Critical areas subjected to degradation are identified by arrows. Although the 'gate sinking' resulting from the unstable Schottky contacts was identified as one of the major failure mechanisms of GaAs MESFETs and HEMTs, the Schottky contacts on GaN appear to be normally stable and no 'gate sinking' effect of DC bias has been reported until now, despite of some findings of changes in the Schottky barrier height after some thermal treatments [17],[18]. For the ohmic contacts, minor degradation with less than 2% variation of fresh condition was found during a 2000-h thermal storage test in the nitrogen atmosphere at 340*C [19]. A more systematic study of the stability of the Schottky and ohmic contacts is still needed, but this kind of degradation is much more moderate compared to the others. Surface trapping-detrapping of electrons at surface states has been suggested as a possible mechanism responsible for the RF current slump and dispersion, which lead in changes of the maximum drain current and knee voltage resulting in reduced power and gain. This kind of trapping can compensate part of the surface component of the spontaneous polarization .............. . ... I. I. -I -........... -.... .1 working as a 'virtual gate' between the actual gate and drain, and hence reduce the 2DEG electron concentration [20]. Another well-know failure mechanism of GaAs-based devices is the hot electron-induced device aging [21],[22], which has also been invoked to explain the current collapse and gatelag effects in GaN-based HEMTs. There are many excellent work reviewing on this topic, especially those working on the characterization of hot-electron effects by the electroluminescence (EL) microscopy [23]. In this thesis, we study in detail the degradation due to inverse piezoelectric effect. Since the uniqueness of the GaN-based HEMTs, high vertical electric field is created at the drain edge of the gate, which would be seen in our simulations and measurements later. When the electric field or the applied voltage reach a critical value, the gate leakage current starts to jump resulting from the trap generations. And eventually strain relaxation and crystallographic defect formation take place in the device layers. A specific hypothesis relating to the inverse piezoelectric effect has been recently formulated by some authors [24],[25], however, an accurate and complete understanding of the physics behind this degradation mechanisms is still needed. In this thesis, we present a simulation, modeling and measurement framework for the purpose of studying this piezoelectric induce degradation. We have also identified thermoreflectance measurements is a powerful technique to evaluate device reliability. 1.3 Thesis Outlines The thesis is organized in the following way: In Chapter 2, we develop self-consistent electro-thermal simulations of GaN-based HEMTs in order to estimate the electric field and lattice temperature of two types of fabricated devices. The simulated and measured IV curves of those devices are compared to evaluate the accuracy of the simulations. In Chapter 3, we use for the first time thermal-reflectance measurements of the surface lattice temperature of the AIGaN/GaN HEMTs to test the accuracy of the thermal part of the simulations developed in Chapter 2. The experimental results of the peak lattice temperature match the previous simulation data very well. Moreover, we found an interesting feature of the thermal-reflectance measurements that could be used as an easy and fast tool for the reliability testing of the AIGaN/GaN HEMTs. In Chapter 4, with the simulation data of the electric field and lattice temperature obtained in Chapter 2 and verified in Chapter 3, we established a new piezoelectric-thermal model for the calculations of the mechanical characteristics such as strain, stress and elastic energy density in the AIGaN layer of a HEMT under various bias conditions, which are very important for the prediction of the reliability in the failure modes of the inverse piezoelectric-induced degradation. In Chapter 5, we use thermo-reflectance measurements to study device degradation as a function of reverse-gate-bias step stress. CHAPTER 2 SELF-CONSISTENT ELECTRO-THERMAL SIMULATIONS 2.1 Introduction Through decades of research in semiconductor physics, a basic set of equations and models has been developed to understand and predict the performance of semiconductor devices including GaN-based HEMTs [26]. The commercial software Silvaco Atlas is a device simulator which incorporate many of these equations [27], and we have used it to simulate the electrical and thermal characteristics of the AIGaN/GaN transistors we fabricated in lab to obtain the electric field and lattice temperature distributions in the cross section of the devices and to analyze key features in the AIGaN layer that will be investigated in the latter chapter. 2.2 Basic Semiconductor Physics Inthis section, the basic equations used by our device simulator are reviewed. 2.2.lPoisson's Equation Poisson's equation is one of the most fundamental equations in the theory of semiconductor devices [26]. It has the following form: div(EV y/) = -p (2.2.1-1) where tp is the electrostatic potential, E is the local permittivity and p is the local space charge density. Poisson's equation relates the electrostatic potential to the space charge density. The reference potential can be defined in various ways. For the software Silvaco Atlas that we are using in the thesis, the reference potential is always the intrinsic Fermi potential of the device [27]. 2.2.2 Carrier Continuity Equations The carrier continuity equations are another set of fundamental equations of device physics which have the following simple and very intuitive forms [26]: oh 1 -=-div , + G - R (2.2.2-1) q -divJP,+ G, - R, (2.2.2-2) where n and p are the electron and hole concentration, Jn and Jp are the electron and hole current densities, Go and Gp are the generation rates for electrons and holes, Ra and Rp are the recombination rates for electrons and holes. Carrier continuity equations connect the carrier concentration to the carrier current densities and generation-recombination rates, offering an important link to the device performance. 2.3 Drift-Diffusion Model Poisson's equation and carrier continuity equations provide the general framework for semiconductor device simulations. But they are not sufficient to simulate devices. Further secondary equations are needed to specify particular models for current densities and generation-recombination rates. The current-density equations, or charge transport models, are usually obtained by applying approximations and simplifications to the Boltzmann transport equation [28]. Those assumptions can result in a number of different transport models such as the drift-diffusion model, the energy balance transport model or the hydrodynamic model. In this thesis, we use the simplest model of charge transport, the drift-diffusion model, which is accurate enough for our simulations of the electrical characteristics of GaN-based transistors. As we will see in the later part of this chapter, excellent agreement between simulations and experiments have been obtained. 2.3.1 Drift-Diffusion Transport Equations In the framework of the drift-diffusion model [28], the current densities are expressed in terms of the quasi-Fermi levels On and Op as the following: Jn = -qpnnV #n (2.3.1-1) JP = -qp pV #, (2.3.1-2) where pn and pp are the electron and hole mobilities. The quasi-Fermi levels On and Op are linked to the carrier concentrations and the potential through Boltzmann approximations: n = n i, exp kTL - 2313 p = ni, exp (2.3.1-4) k TL- _ where nie is the effective intrinsic concentration, TL is the lattice temperature and tp is the electrostatic potential. These two equations can be re-written to define the quasi-Fermi potentials: kT n , = V_ TL in q (2.3.1-5) nie O, - V k in p q (2.3.1-6) ni By substituting these equations into the equation 2.3.1-1 and the equation 2.3.1-2, the following conventional formulas of the drift-diffusion transport equations are obtained: J= qnpE +qDVn 5n V kT (2.3.1-7) q J, = qppE, -qDVp, Z, =-V(v_ kL Ine(2318) q If we are not considering the lattice heating effect, we just set the local lattice temperature as constant e.g. 295K, and self-consistently solve the three sets of equations (Poisson's equation, carrier continuity equations and drift-diffusion transport equations) under specific device domains and structures, to get all of the electrical characteristics such as electrostatic potential, electric field, current densities, etc in the device. Although these simulations results match the measurements quite well under low bias conditions, at higher bias, as the lattice heating plays a more and more important role to the electrical performance of the real device, this model becomes inaccurate (see the black dashed line in Figure 2.6.2-1 and 2.6.2-2 in the latter section). In addition, these simulation results do not include any data on the lattice temperature of the device, which will be heavily used in our further calculations in the latter chapters. So, it is necessary to introduce another two important models: lattice heating model and mobility model into our simulations. 2.4 Lattice Heating Model Silvaco Atlas allows us to calculate the lattice temperature distributions in semiconductor devices using its lattice heating model [27]. This model consists of several sets of heat-transfer related equations, which can be combined with the drift-diffusion model for self-consistent simulations. 2.4.1 Lattice Heat Flow Equation The first fundamental equation of the lattice heating model is the intuitive lattice heat flow equation: C =V(V TL)+ H (2.4.1-1) And in the steady state: V(KVTL) + H = 0 where C is the heat capacitance per unit volume, generation and TL is the local lattice temperature. (2.4.1-2) K iSthe thermal conductivity, H is the heat 2.4.2 Modified Drift-Diffusion Equations In the framework of the lattice heating model, the electron and hole current densities are modified to account for the spatially varying lattice temperatures: J= -qn(V, +PVTL) (2.4.2-1) J, = -qpp(V$, + PVTL) (2.4.2-2) where Po and Pp are the absolute thermoelectric powers for electrons and holes. Conventionally, Pn and Pp are modeled as follows [27]: k q P n N, (ln 3 2 - (2.4.2-4) ) For simplicity and fast convergence of the simulation, in this thesis we will just use the normal drift-diffusion equations as the equations 2.3.1-7 and 2.3.1-8. 2.4.3 Heat Generation Equations When carrier transport is handled in the drift-diffusion model, the heat generation term, H, has the following form: H =q" +q " -qT(J,,VP,))+qTL JpVPp)+q(R -G)[TL pp pann -qTL Ird + + Pn ]divJn -qTL n,p bnJ -IT -)& P ( p n,p and in the steady state, the current divergence can be replaced with the net recombination. Equation 2.4.3-1 then simplifies to: +q(R-G)[p, -, +q H=[q lnn p+TL (Pp (2.4.3-2) lpp In the above equation, the heat generation could be separated into three terms, each of which has its own physical meaning: " q +q lnn is the Joule heating term; ppp is the recombination-generation heating and cooling term; * q(R - G)[#, - * -qTL(JnVPn +JPVPp)is the term of the Peltier and Thomason effects. n+ TL (P -Pn)] In our simulations, also for the reason of easy and fast convergence, we only calculate the Joule heating term for the heat generation. This term can be re-written in a simpler and form as follows: H = (Jn + J,) - E (2.4.3-3) 2.4.4 Thermal Boundary Conditions To solve the lattice heat flow equation in the device domain, the thermal boundary conditions must be specified: ( J,,, 5) a(T - T,)t (2.4.4-1) where a is either 0 or 1,Jtot is the total energy flux and s is the unit of the external normal of the boundary. The projection of the energy flux onto s is: (J -i) L + (TLpn 0 + On)jn + (TLpp + Op)jp (2.4.4-2) When a=0, equation 2.4.4-2 specifies a Dirichlet boundary condition (fixed boundary temperature). In this thesis work, we use Dirichlet boundary condition for all thermal simulations, which implies that we set the bottom of the device substrate at fixed room temperature 295K. 2.5 Mobility Model Electrons and holes are accelerated by electric fields, but lose momentum as a result of various scattering processes. These scattering mechanisms include lattice vibrations (phonons), impurity ions, other carriers, surfaces, and other material imperfections. Since the effects of all of these microscopic phenomena are lumped into the macroscopic mobilities introduced by the transport equations, these mobilites are therefore functions of the local electric field, lattice temperature, doping concentration, and so on. Mobility modeling is normally divided into two areas: * Low field behavior * High field behavior The low electric field behavior has carriers almost in equilibrium with the lattice and mobility has a characteristic low-field value that is commonly denoted by the symbol Pno,po. The value of this mobility is dependent on phonon (lattice temperature) and impurity scattering (impurity concentration), both of which act to decrease the low field mobility. The high electric field behavior shows that the carrier mobility declines with the electric field because the carriers that gain energy can take part in a wider range of scattering processes. The mean drift velocity no longer increases linearly with the increasing electric field, but rises more slowly. Eventually, the velocity does not increase any more with the increasing field but otherwise drops and at the end it saturates at a constant velocity. This constant velocity is commonly denoted by the symbol vsat. This behavior can be well modeled by the Monte Carlo Simulations shown in the Figure 2.5-1 below: ........................................... ........................... x 2.5- Velocity Saturation Model of AIGaN/GaN HEMTs e 0' 0.5 @T=300K 0 0.2 0.4 1.4 1.2 1 0.8 0.6 Lateral Electric Field (MV/cm) 1.6 1.8 2 Figure 2.5-1: Monte Carlo simulations of the electron velocity in AIGaN/GaN HEMTs as a function of the lateral electric field [29]. 2.5.1 Low Field Mobility Model of AlGaN/GaN HEMTs Based on the Monte Carlo simulations [29], the general expression for the low field mobility of AIGaN/GaN transistors used in the drift-diffusion simulations can be fitted : yo(TL,N) =p'in -~ fl4(2.5.1-1) where TL is the local lattice temperature and N is the local (total) impurity concentration. The values of a, @1, P2, 13, 04, pmin, Pmax, Nret that we used in out simulations are listed in the following table: modeled by equation (2.5.1-1) is plotted in the Figure 2.5.1-1: Al3aN/fUaN ritiVi IS ~700 600 o500 e r,400 300 200 310 3 32 370 350 3 3 Lattice Temperature / K 380 390 400 Figure 2.5.1-1: Low field electron mobility in AIGaN/GaN HEMTs as a function of the lattice temperature. From the figure above, we can see that the low field electron mobility in GaN drops from -1000 cm 2N*s to -130 cm2N*s as the lattice temperature increases from 300K to 400K. 2.5.2 High Field Mobility Model of AlGaN/GaN HEMTs According to the reference [29], the general expression for the high field mobility of AIGaN/GaN transistors used in the drift-diffusion simulations has the following formulation: o ( TL,N ) + = E a -1+ E C) n2 v a E n -1" E +L- (2.5.2-1) ni EC where po(TL,N) is the low field mobility modeled in equation 2.5.1-1, and E is the local electric field. The values of vsat, a, n1, n2, Ec we used in our simulations are listed in the following table: vsat(10cm I s) GaN 1.3 a n, n2 E,(kV /cm) 7.0 4.5 0.7 215 The high field mobility behavior modeled by the equation (2.5.2-1) is plotted in the Figure 2.5.2-1: ............ .... .... ... 1000 900 800 High Field Mobility Model of AIGaN/GaN HEMTs 700 E 600 500 C 400 e LLI00 @T=300K 100 00 0.2 0.4 0.6 0.8 1 1.2 1.4 1.6 1.8 2 Lateral Electric Field / (MV/cm) Figure 2.5.2-1: Electron mobility in AIGaN/GaN HEMTs as a function of the lateral electric field at T=300K. From the figure above, we can see that the high field electron mobility in GaN drops from -1000 cm2N*s to -0 cm 2N*s (i.e the electron velocity saturates) as the lateral electric field increases from 0 to 2 MV/cm at 300K. 2.6 Simulation Results Using the drift-diffusion model, lattice heating model and specific mobility models for AIGaN/GaN HEMTs and correctly setting all of the material parameters including band gap, density of states, electron affinity, permittivity, thermal conductivity, etc., we have simulated the electric field and lattice temperature distribution. There is a lot of excellent work in the literature regarding the simulations of the electrical performance of AIGaN/GaN HEMTs [30] [31], but very little on the simulations of the thermal performance [32]. Therefore, this chapter of the thesis focuses mainly on the lattice temperature simulations of the AIGaN/GaN transistors. It also discusses the electrical performance of the devices to test the accuracy of the physical models used. .. ...... ... 2.6.1 Transistors Structures The simulated transistors have exactly the same structures of our real AIGaN/GaN HEMTs, which were fabricated following our standard technology. In order to investigate into the effect of different substrates on the lattice temperature distribution in the device, we fabricated the same AIGaN/GaN HEMTs structures on SiC (transistor A) and Silicon substrates (transistor B) respectively. The following figures show the structures of our two types of transistors: 2pim 2pm Figure 2.6.1-1: Schematic structure of Transistor A Figure 2.6.1-2: Schematic structure of Transistor B 2.6.2 IV Curves The DC current measurements and the simulation data of Transistor A and Transistor B are shown in the Figure 2.6.2-1 and 2.6.2-2. We can see that the experimental and simulated IV curves of both transistors are in perfect agreement and a clear difference between using models with and without lattice heating models (black dashed lines). _ . --:::-::::::: :: ; : : _:-Z;-:::::::::: "_:::: :::::: -- ... .- .......... ............ . ..... - experimert simulation T sLattice heating effect TransistcirA 600 I E ~2W ISO 6 3W 02 7 8 9 1 100 50 1 Vds I V Figure 2.6.2-1: Measured (dot) and simulated (solid line) IV curves of transistor A. The black dashed line indicates the calculated IV curve at Vgs=2V without lattice heating models. 2 3 4 6 5 Vd i 7 8 9 10 V Figure 2.6.2-2: Measured (dot) and simulated (solid line) IV curves of transistor B. The black dashed line indicates the calculated IV curve at Vgs=2V without lattice heating models. From the IV curves above, we also find that the drain-to-source current of Transistor A is larger than in Transistor B. This is because of the better quality and lower defects densities of the sample grown on the SiC substrate, which create fewer buffer traps than in the sample grown on the Silicon substrate. The excellent agreement between the experiment and simulation results of the DC performance of the AIGaN/GaN HEMTs provide a strong proof of the accuracy of the physical models we are using in the simulations and also validate the framework of the self-consistent electro-thermal method used to simulate the electric field and the lattice temperature distribution in the AIGaN/GaN HEMTs, both of which are much more difficult to measure in reality. 2.6.3 Electric Field Distribution The vertical and lateral electric fields across the device in the AIGaN lattice above the channel are extracted from the simulation data for both transistors: 2 - ---Vg=V Vd=12V - VpfWVVds=15 ---Vgs=0Vs=15y --- vgs=uy vOs-Ie Vgs=OVVds=15V 2- -Vg s4Vd s-1I8V 1C'1.5 5 0.5 Source 1 0 L Gate 15 2 26 Microns 3 36 Drain 4 Source 45 W5 1 Gate _ 2.5 Microns 15 Drain _ 3 3.5 4 4.5 Figure 2.6.3-1: Simulation of the vertical electric field Figure 2.6.3-2: Simulation of the vertical electric field along the AIGaN layer of transistor A under increasing along the AIGaN layer of transistor B under increasing drain-to-source bias at Vgs=OV. drain-to-source bias at Vgs=OV. - - Vgs-OV Vdsw3V i2 - -- 1 - -o -Vgt=V Vds=3V Vgs=V Vds=6V Vs=0V Vds=9V TransistorA Vgs=VVds=6V -- Vgs=0V Vds=9V Vgs=cV Vds=12V Vgs=0V Vds-15V Vg=V Vd=18V - Transistor B Vgs=OV Vds=12V -- Vgs=V Vds=15V Vgs9OVds=1V 0 I1 0.68 3 0.4 e- Source 4 : Gate Source : Gate 0 - Drain -, Drain -+ I. ~ 1 1.5 2 2.5 Microns 3 3.5 4 4.5 W5S 1 1,5 2 2.5 Microns 3 3.5 4 4.5 Figure 2.6.3-3: Simulation of the lateral electric field Figure 2.6.3-4: Simulation of the lateral electric field along the AIGaN layer of transistor A under increasing along the AIGaN layer of transistor B under increasing drain-to-source bias at Vgs=OV. drain-to-source bias at Vgs=OV. 23 2.5 -Vg-2V - Vds=16V --- 7 Vgs-3VVde=18V Vgs=-3V Vds=18V . .5 . w 0-6os-- Source Drain 0.5S- Source Drain Gate 1 5 1.5 2 2.6 Gate 3 3.5 4 4.5 Microns B6 1.6 2 2.6 Micrors 3 3' A 46 Figure 2.6.3-5: Simulation of the vertical electric field Figure 2.6.3-6: Simulation of the vertical electric field along the AIGaN layer of transistor A under decreasing along the AIGaN layer of transistor B under decreasing gate-to-source bias at Vds=18V. gate-to-source bias at Vds=1 8V. Vgs=2V Vds=18V 1.6 14 - TransistorA -- Vgs=VVds1BV Vgs=(V Vds=18V Vgs-lVVds18V Vgs=OV Vds=18V VgS-1VVds=18V 6 Vg--t VVds=18V Vgs=-2VVds=18V V_-2VVds=18V 4 Vgs--3V Vde-18V 12 -Vgs-3V Vds=18V 2 6 0.6 0. 4 0.4 0.2 WS Transistor [! Source 1 1.5 2 2.5 Microns 2-Source Drain Gate 3 3.5 4 45 i ;Gate 1A 2 25 Drain -- -3 3.5 A A Microns Figure 2.6.3-7: Simulation of the lateral electric field Figure 2.6.3-8: Simulation of the lateral electric field along the AIGaN layer of transistor A under decreasing along the AlGaN layer of transistor B under decreasing gate -to-source bias at Vds=1 8V. gate -to-source bias at Vds=18V. From the figures above, both the lateral and vertical electric fields peak at the drain edge of the gate, rise as the increasing drain-to-source voltage and drop as the decreasing gate-to-source voltage. In addition, the very similar electric field profiles of Transistor A and Transistor B result from the same device scales and structures regardless of the different substrates and defect densities. 2.6.4 Lattice Temperature Distribution The lattice temperature distributions across the device in the AIGaN layer above the channel are also extracted from the simulation data for both transistors: 3N . I I I 1 330 . 315 '310 2 5 3,5 25A Microns 4 2.5 Microns 45 Figure 2.6.4-1: Simulation value of the lattice Figure 2.6.4-2: Simulation value of the lattice temperature along the AIGaN layer of transistor A temperature along the AIGaN layer of transistor B under increasing drain-to-source bias at Vgs=OV. under increasing drain-to-source bias at Vgs=OV. 3Z- Vgs-3VVds-I8V 3- 310 305 1 1. 2 2. 3 3. 4 45 05 Microns 300- 4 1 5 Gate 2 2.5 Micrers 3 3.5 4 4.6 Figure 2.6.4-3: Simulation value of the lattice Figure 2.6.4-4: Simulation value of the lattice temperature along the AIGaN layer of transistor A temperature along the AIGaN layer of transistor B under decreasing gate-to-source bias at Vds=18V. under decreasing gate-to-source bias at Vds=1 8V. In these figures, we also find that the peak lattice temperature happen at the drain edge of the gate for both transistors. The reason for this is that the peak lateral electric field in the channel at the drain edge of the gate generates the highest heat dissipation therefore the highest lattice temperature, as demonstrated in equation 2.4.3-3. Moreover, from the equation 2.4.3-3 and 2.4.1-2, we can see that for the same material (same thermal conductivity), the lattice temperature is proportional to the output power in the device. Therefore, since the current of the Transistor A is larger than that of the Transistor B under the same bias conditions, the lattice temperature of Transistor A should be larger than that of the Transistor B. However, this is not the case in the figures from 2.6.4-1 to 2.6.4-4, where the lattice temperatures of Transistor A are almost the same as those of Transistor B under the same bias conditions. Actually, this is exactly what we want to see. Due to the fact that the thermal conductivity of SiC material is nearly four times larger than the thermal conductivity of Silicon material, heat, is therefore more easily dissipated from the device into the substrate for Transistor A, causing the lattice temperatures along the channel drop faster despite of the higher power. 2.7 Summary In conclusion, by using the commercial software Silvaco Atlas, we successfully modeled and simulated the electrical and thermal characteristics of the standard AIGaN/GaN HEMTs, which were fabricated on wafers with different substrates (SiC and Silicon). The simulated drain current of the devices matches perfectly with the experimental data, and the effect of the substrate on the lattice temperatures in device performance was also simulated in the simulations as expected. To provide more confidence in this self-consistent electro-thermal simulation, the lattice temperatures data generated in this chapter will be compared with the measurement results in Chapter 3. CHAPTER 3 THERMO-REFLECTANCE MEASUREMENTS 3.1 Introduction Thermo-reflectance microscopy is an important imaging tool for measuring surface temperature distributions [33]. Since it does not require direct physical contact of the surface as opposed to the use of thermocouples, and it offers better spatial resolution than IR (infrared) thermal imaging, and micro-Raman spectroscopy [34], thermo-reflectance microscopy finds many applications in physics and engineering, such as device failure analysis and design optimization [35]. 3.2 Theory Thermo-reflectance microscopy is based on the fact that the reflectivity of a surface depends weakly on its temperature. To first order, the fractional change in the sample's reflectivity ARIR ( AR refers to the change in reflectivity and R is the total reflectivity) in response to surface temperature variations AT is proportional to AT: A 1= AT where R oT =R4R 18AR AR R R (3.2-1) # is the so-called thermo-reflectance coefficient, a characteristic of the specific material [36] and wavelength of illumination [37]. Knowledge of the material-dependent thermoreflectance coefficient , which has typical value ranging from 10' to IV K-', enables the calculation of AT from the measured ARIR. :.............. ............ . ............. 3.3 Experimental Setup The setup of the thermo-reflectance measurements is schematically shown in the figures below: CCD Camera CCD Camer LiLght h Light Source1 Figure 3.3-1: Schematic diagram of the thermo- Figure 3.3-2: Schematic diagram of the thermoreflectance imaging apparatus used for the reflectance imaging apparatus for the calibration of the measurement of AIGaN/GaN transistor. thermo-reflectance coefficient of the surface material. A light-emitting diode (LED) is used to illuminate the surface of the tested devices. The reflected LED light is collected through a standard reflectance-mode microscope objective and imaged onto a CCD array with a resolution of 652x400 pixels. An optical spatial resolution of 150±10 nm is obtained using 467nm (blue) LED light, and a 100x, NA=0.8 microscope objective, which is in quantitative agreement with Sparrow's criterion. The temperature of the sample in Figure 3.3-1 is modulated using a square voltage source of frequency co. The CCD camera then takes images of the sample at a frequency phase-locked to the excitation. To detect the amplitude of Joule heating, the camera takes images of the device at a trigger frequency of 8M, since the temperature change from this heating has a frequency of 2w. In this case the sequential images (each separated by a difference of rr/2 of the phase of the temperature oscillation) are accumulated in 4 image buffers, denoted as 11, 12, 13, and 14. The main quantity of interest is the magnitude normalized change in reflectance R, denoted AR/R, and related to the image buffers by: 28 AR zr (I -1I3)2+(I2_) 2 R - 2 I, + I2 + I, + (3.3-1) 4 Once the ARIR image is obtained, it remains to calibrate the ARIR map to the temperature scale. The system of calibration is shown in Figure 3.3-2. A flat, uniform sample of the material of interest (GaN cap layer for Transistor A and Transistor B) is placed on a thermo-couple attached with a heat sink (a bulk of copper). The temperature of the thermo-couple (and the sample) is modulated using a square voltage bias. A thermo-reflectance image of the sample is obtained in the above manner. A small thermocouple is used in order to ensure good thermal contact, for fast response time, and to minimize any error in the temperature measurement caused by parasitic heat conduction through the thermocouple wires. A low numerical aperture lens is used to avoid parasitic effects due to sample motion from thermal expansion. The (uniform) thermo-reflectance amplitude is then divided by the amplitude of the temperature oscillation as determined by the thermocouple, giving the thermo-reflectance coefficient P. Thermo-reflectance maps of the material can then be easily converted to temperature images. 3.4 Experimental Results In this section of the chapter, the first thermo-reflectance images of AIGaN/GaN HEMTs are demonstrated and analyzed. These high-resolution images (-100nm) of lattice temperature provide a lot of information of the measured device including the important defects densities and distributions, which have. traditionally been very difficult to test. 3.4.1 Calibration of Thermo-Reflectance Coefficient Based on the fact that different materials have different thermo-reflectance coefficients [36], in order to obtain the lattice temperature maps on the GaN cap layer of Transistor A and Transistor B, calibration of the GaN surface material is needed. Since the thermo-reflectance coefficient also slightly changes with temperature, we measured the variation of the thermoreflectivity as a function of the variation of the temperature at 300K, 320K and 340K. The results are shown in the figures below respectively. 0.000s5 - GaN @ T = 300K 0.00050 - 0.00045 - 0.00040 - = (2.64±0.30)x104 0.00035- 0.00030 ).4 0.6 0.8 1.0 1.2 1.4 Figure 3.4.1-1: Variation of the thermo-reflectivity as a function of the variation of the lattice temperature measured on GaN sample and started with 300K. The slope of the fitting line is the thermo-reflectance coefficient. 0.0011 - GaN @ T = 320K 0.0010 - 0.0009 - 0.0008 0.00071 P= (2.70±0.08)xlO-4 0.0006- 0.00051 ,T 2.0 I 2.5 3.0 3.5 4.0 4.5 AT Figure 3.4.1-2: Variation of the thermo-reflectivity as a function of the variation of the lattice temperature measured on GaN sample and started with 320K. The slope of the fitting line is the thermo-reflectance coefficient. .................. 0.0020 GaN @ T = 340K a 0.0018- 0,0016- 0.0014 - 0.0012 -f = (2.80±0.83)x104 0.0010 1.0 1.5 2.0 2.5 3.0 3.5 4.0 \T Figure 3.4.1-3: Variation of the thermo-reflectivity as a function of the variation of the lattice temperature measured on GaN sample and started with 340K. The slope of the fitting line is the thermo-reflectance coefficient. We find that the linear relationship of AR/R and AT holds well for the temperature rages of interest and the thermo-reflectance coefficient varies very little (<10%), which gives us an error of less than 2% (-5K) in ternerature. Jherefore, it is statistically reasonable to treat the average thermo-reflectance coefficient measured by the calibration as the theoretical one involved in the temperature calculation. By averaging the data above, we obtain a thermoreflectance coefficient of 2.73x1 0-4 K-1 for GaN material under the 467nm (blue) LED light. 3.4.2 Lattice Temperature Distribution Using the thermo-reflectance coefficient obtained in the calibration and converting the thermoreflectivity maps into lattice temperature, we obtained accurate data for the lattice temperature distribution on the GaN cap layer of Transistor A and Transistor B. Figures 3.4.2-1 to 3.4.2-12 show the lattice temperature profiles of Transistor A and Transistor B from Vds=3V to Vds=1 8V (step 3V) at Vgs=OV. The scales of the GaN cap layer bands in each image are 1.5 pm wide and 40 pm long and the resolution is about 150 nm. Transistor A Transistor B K TVmpr"*- / Drain :5 Drain 3M0 326 320 316 310 3M5 3M6 Figure 3.4.2-1: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=OV, Vds=3V. I Drain Figure 3.4.2-2: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=3V. I 9mper1ure/K 3A5 340 Drain 3315 30 326 320 Gate 316 1U 206 Source Figure 3.4.2-3: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=OV, Vds=6V. I Drain Figure 3.4.2-4: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=6V. ' erx/ K 346 3410 Drain 336 3M0 326 X20 310 306 3011) 295 Figure 3.4.2-5: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=OV, Vds=9V. Figure 3.4.2-6: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=9V. 1Umpeture/K Drain 3A" 340 I Drain 336 3130 Gate 326 320 310 Source 306 Figure 3.4.2-7: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=OV, Vds=1 2V. Drain Figure 3.4.2-8: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=12V. 3'46 340 I Drain Gate 316 310 Source 306 Figure 3.4.2-9: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=OV, Vds=1 5V. Drain Figure 3.4.2-10: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=15V. T Jvcab 340 I Drain 326 320 315 30 Source Figure 3.4.2-11: Top view of the lattice temperature distribution on the GaN cap layer of Transistor Aat Vgs=OV, Vds=1 8V. 300 Figure 3.4.2-12: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=OV, Vds=1 8V. Figures 3.4.2-13 to 3.4.2-23 below show the lattice temperature profiles of Transistor A and Transistor B from Vgs=2V to Vgs=-3V (step -1V) at Vds=1 8V. The dimentsions of the GaN cap layer bands in each image are also 1.5 pm wide and 40 pm long and the resolution is still about 150 nm. Transistor A Drain Gate Source Figure 3.4.2-13: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=2V, Vds=1 8V. Drain Gate Source Figure 3.4.2-14: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=1V, Vds=1 8V. Temprature/ K Drain Gate Source Figure 3.4.2-1.5: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=0V, Vds= 18V. Tempermur/ K Drain Gate Source Figure 3.4.2-16: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=-1V, Vds=1 8V. Temperature/K Drain 326 320 Gate 315 310 30S Source Figure 3.4.2-17: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=-2V, Vds=1 8V. Drain Gate Source Figure 3.4.2-18: Top view of the lattice temperature distribution on the GaN cap layer of Transistor A at Vgs=-3V, Vds= 18V. amo Transistor B Drain TempetuM I -370 Gate Source Figure 3.4.2-19: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=1V, Vds=1 8V. Drain Gate Source Figure 3.4.2-20: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=0V, Vds=18V. Drain Gate Source Figure 3.4.2-21: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=- 1V, Vds= 18V. -"'raturef I 37 Drain Gate Source Figure 3.4.2-22: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=-2V, Vds=1 8V. Dra in Temperature /I -370 Gate Source Figure 3.4.2-23: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=-3V, Vds=1 8V. The above lattice temperature distribution images of Transistor A and Transistor B have important and interesting features: e e For both Transistor A and Transistor B, the lattice temperatures in the drain-to-gate area and gate-to-source area increase with increasing drain-to-source voltage and decrease with decreasing gate-to-source voltage. This feature is consistent with the simulations results we demonstrated in the Figures 2.6.4-1 to 2.6-4-4 in Chapter 2 and will be analyzed in detail in the section 3.4.3; For Transistor B, the lattice temperature distributions are not uniform in both the drainto-gate and gate-to-source regions compared to the fairly uniform distributions of Transistor A. Some areas are heated as hot as 370K, but some ones are almost at the room temperature. This interesting feature could be explained by the different defect ... ................ densities in the AIGaN layers as well as by the different thermal conductivity of the substrate and will be discussed in detail in the section 3.5; Comparing Transistor A and Transistor B under the same bias conditions, we find that the lattice temperature of Transistor B is much higher (>20K) than Transistor A. This difference is because the SiC substrate of Transistor A, with much higher thermal conductivity than the Si substrate of Transistor B, dissipates heat more efficiently hence cools the surface temperature of the GaN cap layer, as predicted in the simulation results in Chapter 2. 3.4.3 Experiment vs. Simulation Since the lattice temperature distributions of Transistor B are not uniform, in this section we only use the experimental data of Transistor A. By averaging the lattice temperature along the gate-width direction, we compare them with the simulation results obtained in Chapter 2 as shown in the figures below: 3201 S315 *315 Vds=1V E NW I-310 I-310- Microns '5 4 4 55 Microns Figure 3.4.3-1: Measured and simulated lattice Figure 3.4.3-2: Measured and simulated lattice temperature along the GaN cap layer in the gate-to- temperature along the GaN cap layer in the drain-tosource region of Transistor A under the decreasing Vds gate region of Transistor A under the decreasing Vds at at Vgs=OV. Vgs=OV. 340 Gate Source +-- TransistorA 335 --- @Vds=18V - 330 - - experiment simulation 325 320 S320! IV i~315 -L S3101 32E e 4.5 Vp:-IV 0 05 1 15 Microns Micrans Figure 3.4.3-3: Measured and simulated lattice temperature along the GaN cap layer in the gate-tosource region of Transistor A under the decreasing Vgs at Vds=18V. Figure 3.4.3-4: Measured and simulated lattice temperature along the GaN cap layer in the drain-togate region of Transistor A under the decreasing Vgs at Vds=1 8V. 330 -25 experiment 33M 330 -simulation] -l- -experiment -& -sirmulation 320 325 S315 320 310#0 295 296 - 290 Transistor A @ Vds=1SV TransistorA @Vgs=OV 285j 0 2 4 6 8 10 Vds / V 12 14 16 18 26.4 -3 -2 -1 0 1 2 3 Vgs / V Figure 3.4.3-5: Measured and simulated peak lattice Figure 3.4.3-6: Measured and simulated peak lattice temperature on the GaN cap layer of Transistor A as a temperature on the GaN cap layer of Transistor A as a function of Vds at Vgs=OV. function of Vgs at Vds=1 8V. From the Figures 3.4.3-1 to 3.4.3-4, we can see that the match between the shape of the simulation curves of the lattice temperature distribution along the device and with the experimental data is not perfect, but the peak temperatures near the drain edge of the gate are still in excellent agreement with the measurements (see in the Figure 3.4.3-5 and 3.4.3-6). ...... ......... .......... . .... The reason of the difference between experiment and simulation is possibly because of the simplifications done to model the heat flow in AIGaN/GaN HEMTs. The heat flow is largely influenced by the various defects and dislocations in the material. This is especially important for AIGaN/GaN hetero-structures grown on SiC, with 109 cm- 2 defects density, and for those grown on the Silicon substrate with even higher defect density. The variation of the thermal conductivity of materials, the interface between AIGaN and GaN layers and the substrate also play an important role to explain the difference between the experimental and simulated lattice temperature distributions. 3.5 Discussion As we mentioned in the previous section, one of the most interesting features of the experimental results is the non-uniformity of the lattice temperature images of Transistor B and we observed this feature in all devices fabricated on AIGaN/GaN samples grown on the Silicon substrate. The device surface is smooth and clean, and all of the photo-resists have been removed. Therefore, it is quite reasonable to account this non-uniformity to the higher defect densities in Transistor B. Because defects and dislocations limit the heat flow (cool areas), hot 'islands' are created on the surface of the transistor as we observed in the lattice temperature image below: Possible Defects Drain Hot islands *_1, G ate Temerature/ ( Possible Defects ""7" Hot islands *_00 Source Figure 3.4.4-1: Top view of the lattice temperature distribution on the GaN cap layer of Transistor B at Vgs=1V, Vds=1 8V. This feature of the thermo-reflectance measurements for the lattice temperature, actually, provides a very easy and direct tool for the early testing of the reliability of the AIGaN/GaN HEMTs in the terms of the defects densities in the materials. 3.6 Summary To summarize, in order to test the accuracy of the self-consistent electro-thermal simulations, we took the advantage of high-resolution thermo-reflectance microscopy to measure the lattice temperature distributions on the surface of AIGaN/GaN HEMTs. Good agreement with the simulation results in the location and value of the peak temperatures under various bias conditions was obtained, although an improved lattice heating model is needed to reduce the difference between the measurements and simulations. In addition, we found non-uniformity of the temperature distributions along the gate-width direction on wafers grown on Silicon substrate which we associated to the effect of the large defects densities in the wafers. In Chapter 5, we will revisit this interesting feature of the thermo-reflectance measurement and we will use it to study degradation in GaN-based HEMTs. CHAPTER 4 PIEZOELECTRIC-THERMAL CALCULATIONS 4.1 Introduction Since AIGaN and GaN are both piezoelectric materials, the coupling between the electric field, the lattice heating and the mechanical properties gives rise to variations in the strain field and elastic energy densities, which eventually change the electrical characteristics of the AIGaN/GaN HEMTs. This degradation mechanism, called the inverse piezoelectric effect, has been intensively studied recently [25] [38] [39]. However, quantitative analysis of this failure mechanism is still lacking. This chapter aims at providing new understanding of the theory of the inverse piezoelectric-induced degradation and to provide fully-coupled piezoelectricthermal calculations of the mechanical characteristics of the AIGaN/GaN HEMTs for further investigation. 4.2 Theory In this section, we will establish the piezoelectric-thermal model for the calculation of the mechanical characteristics (strain, stress and elastic energy density) in AIGaN/GaN HEMTs. 4.2.1 Fundamental Equation To study the mechanical properties of the AIGaN/GaN HEMT, it is natural to treat it as a whole mechanical system and to start from the fundamental equation of this system. Using the thermodynamic method, the fundamental equation of the AIGaN/GaN heterostructure system can be written in the form of its internal energy density u as follows: U= U(Se,,trop e E,t , Ezz, Er , ,E D,D,,D7 ) (4.2.1-1) where Sentropy is the entropy density, Eij (i,j=x,y,z) are the six components of the strain and Dk (k=x,y,z) are the three components of the electric displacements in the AIGaN/GaN HEMT. These three variables are the independent extensive parameters or the natural variables of the system. The first differential of u therefore has the following formulation: du = e ,Dk ds+ dej + _ 01 J @ i,ja,y,z =xy sentropy,Dk dDk 1 k (4.2.1-2) Sentop, -; The partial derivative terms are called the intensive parameters, and have the following conventional notations: (4.2.1-3) entropy ,D T 014 d-ij ki (4.2.1-4) 0-ij etrp,,Dk 8 (4.2.1-5) = E,k where T is the temperature, aij are the six components of the stress and components of the electric field in the AIGaN/GaN HEMTs. Ek are the three By substituting equations (4.2.1-3) to (4.2.1-5) into equation (4.2.1-2), we have: du=Tds+ Ij(ao-Ispe + 1(Ek)dDk i,j= x,yz k= x,,z This is the first derivative of the fundamental equation. 4.2.2 Equations of State (4.2.1-6) By expressing the intensive parameters in terms of the independent extensive parameters, we have the equations of state: T(T i- = a Ek = E,, - (s eD,.V, E ,Ee DDD (4.2.2-1) (4.2.2-2) ,D,,Dz) E,,,E,,ExEyz ,E 1E, Ek(senUgxE ) (4.2.2-3) DDDz) E, 4.2.3 Alternative Formulation For thermal, electrical and mechanical systems like AIGaN/GaN HEMTs, the independent extensive variables are temperature, strain and electric field. Therefore, we need to use them as our natural variables in the fundamental equation. This leads us to the fundamental equation in the form of the Helmholtz free energy density f: f = f (T,ex,c,e z,,E Y,e,.e, E, E,E )(4231 Using Legendre transform of the internal energy density u, we have: f = u - Tsentropy - EkDk (4.2.3-2) k= x,v,z The first derivative is: df= ( T dT+ - df k,Ek =-s 0)r i,j=xY,z deNjT,Ek entrop dT+ with the conventional notation: k=x,y,z ek)Tejj i, j= x'yz Ek des+ jo-,de DkdEk k=x,y,z dEk (4.2.3-3) (4.2.3-4) C = sentropy (4.2.3-5) (If )Eij,Ek (4.2.3-6) deNj T,Ek (4.2.3-7) =Dk Similarly, according to section 4.2.2 we have the equations of state: ' Sentropy (T,' Sentropy ' zz' xy' Cxz' Syz, Ev V, E,) (4.2.3-8) ijO (Tj xx, Eyy, -Ozz, -Oxy' -xz, -yz , EX ,E,, E,) Dk (4.2.3-9) Dk(T,exx,e) vezzex,, exze,,,Ex,,E,, E7) = (4.2.3-10) 4.2.4 Material Properties The first derivatives of the equations of state or equivalently the second derivative of the fundamental equation gives us the material properties of the system. Firstly, the first derivatives of the equations of state (equation 4.2.3-8 to 4.2.3-10) are: dsentrop = "nrp dT + E (x S """ )T, I.m=x,y 'z mT ,Ek )e1t1,E, dT + e n ,E z- x k dDk= (dI aem,Ek or re-written in the matrix forms: 1.m=x,y,Z " k=x y,z im T,Ek IMxy~ Im del,+ T,Ek k d deln + I dDk ) dT+ del,, + k=x,y,z : n = ,y,z dEk (4.2.4-1) T ej dEk (4.2.4-2) dEn (4.2.4-3) k TeS dDk TE j d dsentropy = -Ce,,E d T [a] dT _[C] + ,E [C T,E ] _ [P a T - E dE (4.2.4-4) d g[e dE (4.2.4-5) - dT + [eT,E]dZ+(pe-nittivity ] dE d = (4.2.4-6) (a E! where -= DJ , E= E2 , , 6= =D2 EV 6 6/ sD3 E6 ) The subscript used here means: xx--1 ,yy--.2,zz--+3,yz--4,zx--5,xy--+6 and x--1 ,y-+2,z-+3. * Thermal Properties ** Specific Heat C,, Ek = Kd (4.2.4-7) EmI.,Ek 4* Thermal Expansion Coefficient aI a2~ [a,E = ai=Q~&J (4.2.4-8) o,,~ ,Ek * Elastic Properties + Elastic Compliance [STE = Si l S12 S13 S14 S15 S16 S21 S22 S23 S24 S25 S26 S3 1 S32 S33 S 34 S35 S3 6 S4 1 S42 S43 544 S4 5 S46 S5 1 S52 553 S54 S55 S56 S61 S62 S63 S64 S65 S66,/ C1I C12 C13 C14 C15 C16 C2 1 C22 C2 3 C24 C2 5 C26 C3 1 C32 C3 3 C34 C3 5 C36 C41 C42 C4 3 C44 C4 5 C46 C51 C52 C5 3 C54 C5 5 C56 C62 C6 3 C64 C6 5 C66 .1 SY= do (4.2.4-9) T ,E, * Elastic Stiffness cTE ] = \C 61 C.. = d I (4.2.4-10) j /T,E, * Piezoelectric Properties + Piezoelectric Strain Constant d11'd [dT]=!d 2 d13 d14 d15 d16 d22 d23 d24 d25 d26 d31 d32 d33 d34 d35 d36 ) d = I (4.2.4-11) dE) + Piezoelectric Stress Constant ]) 0 - e1 1 612 613 e14 e15 e16 21 e22 e2 3 e2 4 e 25 e 26 e31 e32 e33 e34 e 35 e36 / Dielectric Properties =i (4.2.4-12) [ Epermittivity 8 0 _ permittivity permittivity, 1'i2 permittivity 1'i3 ermittivity permittivity -22 permittivity Epermittivity 31 permittivity 32 23 permittivity £33 J ermittivitv eEJ , = (4.2.4-13) Pyroelectric Properties ODi [p]= P2J Pi =a (4.2.4-14) \P3J 4.2.5 Constitutive Relations The constitutive relations play an essential role in the piezoelectric-thermal calculations, because they relate and couple the mechanical, electrical and thermal properties of the materials together. 4.2.5.1 General Constitutive Relations of the Wurtzite IHI-V Nitride For wurtzite Ill-V nitride semiconductor, based on their crystal symmetry, we can simplify the matrixes of the elastic stiffness, piezoelectric stress constant and thermal expansion coefficient in the following way: 0 0 0 0 0 [CT,E ] = (4.2.5.1-1) C6 6 ('0 [eT]= 0 0 se31 0, (4.2.5.1-2) (a> iai Ia [ao,E (4.2.5.1-3) = 0) Meanwhile, we still have the basic constitutive relation for the stress of interest as the first derivative of the equation of state: &=-[cT,E d0 [a A = -[c T,E] [a] T[C,E d T,E d~ eT,E y - d$ A6-[e T,Ei (4.2.5.1-4) d AE t (4.2.5.1-5) Substituting equations (4.2.5.1-1) to (4.2.5.1-3) into equation (4.2.5.1-5), we get the general constitutive relations of the wurtzite Ill-V nitride in matrix form: AU5 0 0 0 0 0 \AU 6 C66 / Au Ao 2 Au AU4 Aei-aaAT AE, Ae 2 - aaAT Ags-acAT 4.2.5.2 Free-Standing and Clamped Model AC4 Ae5 Ae6 e0 0 AE2 AEO' (4.2.5.1-6) .V':V:........ ...... __ _ .... .. .. ....................... Since we have already obtained the electric field and lattice temperature distribution from previous simulation data in Chapter 2, we can now calculated all the components of the strain and stress, which are 12 unknowns. In order to solve these 12 unknowns, for our specific case of AIGaN/GaN hetero-structures as schematically shown in the Figure 4.2.5.2-1 below, we use free-standing and clamped model to reduce the number of unknowns. Figure 4.2.5.2-1 Free-standing implies no vertical (z direction) force on the AIGaN layer of interest because of its free surface. Even if we consider the mechanical influence of the source, drain and gate on the AIGaN layer, the regions of source-to-gate and gate-to-drain are still free-standing. Therefore, we have: AU3 =AU 4 =AU5 =0 (4.2.5.2-1) Also, since the transistor is totally symmetric along the y direction as shown in the Figure 4.2.5.2-1, we must have: AE2 = Ae 4 = AE 6 =0 ( (4.2.5.2-2) Moreover, the clamped model indicates that the boundaries of the transistor along the channel (x direction) are fixed, which means no displacement on x direction on the boundaries. So, we get: uxL = Ux L (4.2.5.2-3) 0 where u is the displacement and L is the source-to-drain distance as shown in the Figure 4.2.5.2-1. By Substituting equations (4.2.5.2-1) and (4.2.5.2-2) into equation (4.2.5.1-6), then we have 6 equations for 6 unknowns: AU2 0 0 0 Au6 A1l - a 0 0 0 0 0 0 Ae3- acAT 0 0 c4 0 0 0 c11 c12 c13 0 c12 cII c13 c13 c13 c33 0 0 0 0 0 , 0 AT -aaAT AE AE2 0 (4.2.5.2-4) AE3 AE5 0 C6 6 ,1 which can be solved explicitly as follows: 2 2 Au- = C3 3 -e)AE3 +(2_-c C3 3 2 Auo2 = (c12 c3)s l-c 1 2 +( c13e33 )AE3 C - c13 C33 Ac + (4.2.5.2-5) + 2 13 (2--_C 11 I - C12 )aaAT e33 AE3+(2 ci3aa + a)AT C3 3 (4.2.5.2-6) (4.2.5.2-7) AU =0 AE 3 )aaAT C3 3 (4.2.5.2-8) C33 AE5 = e15 C4 4 AE (4.2.5.2-9) 4.2.5.3 The Initial States Because of the lattice mismatch between AIGaN and GaN, the AIGaN/GaN hetero-structure shows an initial strain and stress in its thin AIGaN layer, which is schematically shown in the figure below: H K A1XGajxN AlXGal;(N GaN GaN Substrate Substrate Figure 4.2.5.3-1: AIGaN layer initially experiences tensile strain on GaN layer because of the lattice mismatch between them. Therefore, the initial states of the AIGaN layer in the AIGaN/GaN hetero-structure are as follow: 0 aGaN 20 - '61 F3 aAlGa_,N a_ aAl Gal-N 3 -2 0 £4 =8 o0 = o = (c (4.2.5.3-2) 614 0 (4.2.5.3-3) G6 = = C +c (4.2.5.3-1) l -2 (4.2.5.3-4) C 33 (7 3 = (T4 = E ' = E= s= U 6 = 0 E3=0 T' = 295K (4.2.5.3-5) (4.2.5.3-6) (4.2.5.3-7) 4.2.5.4 Constitutive Relations of AlGaN/GaN HEMTs Substituting the initial state equations (4.2.5.3-1 to 4.2.5.3-7) into equations (4.2.5.2-5 to 4.2.5.2-9), we finally obtain the constitutive relations for strain and stress field in the AIGaN/GaN HEMTs as a function of the electric field and the lattice temperature distribution: 2 2 =i (c11 C2 2 (4.2.5.4-1) c13e33 -el)E 3 +(2 c3 c 11 -C12 )a,(T -295)+Oi c) C3 3 C33 C33 e2 3 )(1 eO)+(C 13e3 C 3 e3 )E3 +(2--c =(c 12 -- )(ei -Ei )+(ci C3 3 C33 C3 3 U3 = U 4 = ( 5 E2 = E3 = -S-3(e C3 3 - E41)+--"-E 3 +(2 1 I -Ci 2 )a(T -295)+ 2 (4.2.5.4-2) = U6 = 0 (4.2.5.4-3) 0 2 (4.2.5.4-4) -SL3a,+a,)(T -295)+ E (4.2.5.4-5) C33 C3 3 4= E5 = E6 = 0 (4.2.5.4-6) 5E (4.2.5.4-7) C44 Now, we only have one unknown variable E1, the strain in the x direction (along the channel). It should be highlighted that E1 is not uniform in the AIGaN layer of interest, in matter of the fact that prevous work wrongly uses the initial strain as the final strain and claims a uniform strain field in the AIGaN layer. 4.2.6 Equilibrium Equations Based on the fact that the transistor is in the mechanical equilibrium and no body-force in it, Newton's second law should be obeyed. So, we have the following equilibrium equations: 6a + ax a76++ a0 ay az -6+ ax 2 + ay at5 + ax -0 _ a_ Jz 4+ 3 a ay (4.2.6-1) -40_ - 0 az By using equation (4.2.5.4-3), equation (4.2.6-1) is simplified as follows: ta2 [',=0 aa2-0 (4.2.6-2) This equation indicates that the stress field in the AIGaN layer is uniform, contradicting the conclusion of previous work [38] [40] [41] that claimed that the applied electric field results in an inhomogeneous stress field in the AIGaN layer. This wrong conclusion is mainly because previous work neglected the mechanical equilibrium conditions of the device. 4.2.7 The Boundary Conditions Problem Substituting equation (4.2.5.4-1) and (4.2.5.4-2) into equation (4.2.6-2), we get two partial differential equations: (c (c 2 a C2 a 2u 2u + )c 13 c33 where D ax = Jx C33 axay + c33 9 C13'3 3 C33 Cle32 -e )E 3 ax a +(2 c-C E3)3 + ay C33 (2cy 11 c -C12 C33 e , using the strain-displacement relations. Because of the symmetry along y direction, -C 3T 12 )a a ay =0 _ (4.2.7-1) -0 (4.2.7-2) 32 E S_ xy 43T 3 (4.2.7-3) =0 y ay So, equation (4.2.7-2) always holds. The problem of solving the strain and stress field in the AIGaN/GaN HEMTs, therefore, becomes a well-defined boundary conditions problem: (c_ u3c {(cl C3(3 ax c1 3e3 3 C33 _ 3x 3 +(2 3 =0 C33 Since we have already obtained the distribution of 2 )aa E3 (4.2.7-4) and T from the simulations in Chapter 2, equation (4.2.7-4) could be solved in Matlab using the finite difference method. As long as we get the distribution of the displacement ux, hence the strain eI in the transistor, the other 11 unknowns of stress and strain could be easily calculated by using the equations (4.2.5.4-1) to (4.2.5.4-7). 4.2.8 Elastic Energy Density The elastic energy density is another important and interesting variable in AIGaN/GaN HEMTs, because defects creation, crack formation and other mechanical failures are all related to the elastic energy density in materials. Due to its essential role, there are numerous studies and calculations of the elastic energy density distributions in AIGaN/GaN HEMTs. However, in this chapter, we derive a new set formulas of the elastic energy density based on the equations we have just established in the above section. The elastic energy density or the mechanical work stored per unit volume in the material has the following intuitive relation with the strain and stress: dW =a de,+ 2 de 2 +u 3 de +q 4 de4 +o 5 de5 +a 6 de (4.2.8-1) Substituting equations (4.2.5.4-3) and (4.2.5.4-4) into the above equation, the elastic energy density of AIGaN/GaN HEMTs has a very simple formulation: dW = or dei (4.2.8-2) Using the equation (4.2.5.2-5), we obtain a formulation of the elastic energy density as a function of the stress, electric field and temperature: CIAe3 _ e31 C dW 12 = "1 o C1 2 2C C13 33 C 33 C2-e1 idE- C11 p123 C, - C12 C2 23 (4.2.8-3) 3 C3 1 aidT C33 C33 Compared to the change of electric field and temperature from the initial state to the final state, the change of stress is actually very small (as we will show in the latter section of this chapter), so we can treat the stress in the last two terms of the equation (4.2.8-3) as constant with the value of the average stress when integrating the other variables as following: C1333_31 W , = 2 C11 2 2 C13 (a,+or)E3 C C123 2 C11-C13 C33 C33 -C C33 2 (CII - C1 12 +$aadi+01)(T-295)+W4 (4.2.8-4) 3 C33 where W = (4.2.8-5) )2 C1 +C12 -2 C1 3 33 is the initial elastic energy density in AIGaN/GaN HEMTs. 4.3 Calculation Results By coding the previous equations in Matlab and extracting the electric field and the lattice temperature data from previous simulations, we solve the PDE equations (4.2.7-4) and obtain the strain, stress and the elastic energy density in the AIGaN layer of AIGaN/GaN HEMTs. 4.3.1 Strain Inthis section, we analyze the different components of the strain data. 4.3.1.1 X Component of Strain (i.e. strain along the channel) -0-Change of the Peak XComponent of Strain 2 66 -- Vgs=VVds=3V -- V=VVdS=0V 6.5 CD / Piezoelectric-Thermal Effect E/ 6.46 3 ;6- sou rce Gate ---- * Drain -4 22 8.2 6.1 0.5 1 1.5 2 2.5 Microns 3 3.5 4 4.5 Transistor A @Vgs=OV // TransistorA 0 - 5 0 2 4 8 8 10 Vds IV 12 14 16 18 Figure 4.3.1.1-1: Value of the x component of strain Figure 4.3.1.1-2: Percentage change of the peak value along the AIGaN layer of Transistor A (SiC substrate) of the x component of strain at the drain edge of the under increasing drain-to-source bias at Vgs=OV. The gate as a function of the drain-to-source bias at black line indicates the initial state. Vgs=OV (Vds=OV state to high-power state). 7 __ _ _ _ __ _ _ _ _ 1U Vs2Vds=18V TransistorA Vse-tVd 68 7 7 - Inverse Pieoelectric Effect 8 -- V -2V Vde9V -- Vgs--3VV-sI1V - 7 V-'OVds-18V -- V /Vd.=ISV 6 66 5- Lattice Heating Expansion O3 0E 1 15 2 TransistorA @Vds=18V 1 -0-Change or the Peak XComponent of Strain -20 -18 2 Miems -16 -14 -12 -10 8 -6 4 -2 0 2 Vgs /V Figure 4.3.1.1-3: Value of the x component of strain Figure 4.3.1.1-4: Percentage change of the peak value along the AIGaN layer of Transistor A (SiC substrate) of the x component of strain at the drain edge of the under decreasing gate-to-source bias at Vds=1 8V. The gate as a function of the gate-to-source bias at black line indicates the initial state. Vds=1 8V (high-power state to off state). From the above figures, we find that in our fully-coupled piezoelectric-thermal model, the strain along the channel direction in the AIGaN layer peaks at the drain edge of the gate for all of the bias conditions, especially for the highly-off state (large reverse gate bias). The peak value can increase up to -10% beyond the initial state (see in Figure 4.3.1.1-4). The physics behind this effect can be explained as follows: According to the constitutive relation (4.2.5.1-4), both the increasing vertical electric field and the increasing lattice temperature in the AIGaN layer tend to tensile the lattice in the x direction (along the channel). In addition, at the drain edge of the gate, as shown in the simulations in Chapter 2, both of them reach the maximum values (Figure 2.6.3-1, 2.6.3-5, 2.6.4-1, 2.6.4-3). Therefore, the strain in the AIGaN layer along the x direction must peak at the drain edge of the gate, in an agreement with the calculations. Moreover, under the conditions of increasing Vds at Vgs=OV, the peak values of the vertical electric field and the lattice temperature both increase with the drain-to-source voltage, so we should also observe the same trend of the peak value of the x component strain in our . ... .... ......... piezoelectric-thermal calculations as shown in Figure 4.3.1.1-2. Similarly, under the conditions of decreasing Vgs at Vds=18V, we have also known from the previous simulations that the peak value of the vertical electric field increases and the maximum lattice temperature decreases to room temperature, therefore, the x component strain must increase as the Vgs decreases in the off state (where no current flow in the AIGaN/GaN HEMTs) and decrease as the Vgs decreases from the high power state to the off state because of the smaller and smaller lattice heating expansion. This trend also matches our piezoelectric-thermal calculations in Figure 4.3.1.1-4. 4.3.1.2 Z Component of Strain (Vertical Strain) X10- Piezoelectric-Thermal Effect --- Vgs=0V Vds=18V a S S4.5- Vgs=0VVds=5V -- -- Vs=OVVds=12V Vgs=0V Vds=9V -V=OVVds=6V -- Vgs=0V Vds=3V 0,5 Transistor A Vds=0V -Vgs=0V 0 Transistor A @Vgs=OV 1 1.5 2 2.5 Microns 3 3.5 $-Change ofthePeak ZComponent of Strain.1 A A.5 5 U 2 4 6 8 10 Vds / V 12 14 16 18 Figure 4.3.1.2-1: Value of the z component of strain Figure 4.3.1.2-2: Percentage change of the downside along the AIGaN layer of Transistor A (SiC substrate) peak value of the z component of strain at the drain under increasing drain-to-source bias at Vgs=OV. The edge of the gate as a function of the drain-to-source black line indicates the initial state. bias at Vgs=OV (Vds=OV state to high-power state). ............ _ _ _ _ _ _ _ _ _ _ _ _ +Sou rce . 35 _ -rain -+ 25 Inverse Piezoelectric Effect -4- 20 I 01 S5 s- v v 18 Vgs.2VVds.18V Veova10 :v rTransistor e v Transistor A -- vgsIO.=18v-v Vgs*.20VVftWSV 5 --gs ;V -S 1.6 .attic Heating Expansion La5c -* Vq=QV~1;=0-L2L MiIS 3 Micron$V 36 4 AS 5 6 - A @Vds=18V Change of the Peak 2 Component of Strain 18 -16 -14 -12 -1 18 q -5 6 -4 2 0 2 a/ Figure 4.3.1.2-3: Value of the z component of strain Figure 4.3.1.2-4: Percentage change of the downside across the AIGaN layer of Transistor A (SiC substrate) peak value of the z component of strain at the drain under decreasing gate-to-source bias at Vds=1 8V. The edge of the gate as a function of the gate-to-source black line indicates the initial state. bias at Vds=1 8V (high-power state to off state). The calculation results of the vertical strain are in perfect consistency with the physics of the piezoelectric relations. Actually it is fairly intuitive that tensiling the lattice in the lateral direction compresses it vertically and the larger the tensiling the larger the compressing. On the other hand, for the lattice heating effect, both directions should be expanded with increasing lattice temperature. More importantly, as we can see from Figure 4.3.1.1-4 and 4.3.1.2-4, under larger and larger reverse gate bias, the lattices at the drain edge of the gate would experience more and more expansion and thinning. In the end, this process will create deep cracks at the drain edge of the gate which have already been observed in some previous work [39] [42]. This kind of failure mechanisms in AIGaN/GaN HEMTs would be measured and discussed in more detail in Chapter 5. 4.3.2 Stress The uniform planar stresses in the AIGaN layer can be calculated in the piezoelectric-thermal model under the various bias conditions as shown in the figures below. ..... . ....... ...... 3.06 - -0 - x component of stressy component of stress 3.05 304 3.03 3.02 * * 3.01 TransistorA %, 'b~.~* ~ N 3 2.99 298 2.971 2.06 0 2 6 4 8 10 Vds i V 12 14 16 18 Figure 4.3.2-1: Value of the x and y component of stress in the AIGaN layer of Transistor A (SiC substrate) as a function of the drain-to-source voltage at Vgs=OV. 3.06 - 3 05. -x component of stress - -y component of stress 3.04 - TransistorA 3.03. 3.02 - M 3. 2.99 297 -20 -18 -16 .14 -12 -10 -8 Vgs / V -6 -4 -2 0 2 Figure 4.3.2-2: Value of the x and y component of stress in the AIGaN layer of Transistor A (SiC substrate) as a function of the gate-to-source voltage at Vds=1 8V. We can see that the changes of the stress in the AIGaN layer are actually very small compared to the changes of the strain, the electric field and the lattice temperature, so we can treat them as constant in the equation 4.2.8-3 in order to simplify the calculations of the elastic energy density. 61 ...................... ... 4.3.3 Elastic Energy Density Finally, the elastic energy densities under various bias conditions are calculated using the equation 4.2.8-4. The results are mentioned in the figures below: A. 8i 22x 10 2 15 -Vgs=VVds=12V V9s=0VVds=9V -Vs=OVVds=6V Vgs=0V Vds=3V Vgs=VVDs=OV 21 25 C Vgs=0VVds=18V Vs=0V Vds=15V - I -'" 4 Piezoelectric-Thermal Effect 3 W 195 Ii 'A -4 - Change of the Peak Elastic Energy Density 19 TransistorA @Vgs=OV TransistorA 0 0.5 1 1.5 2 2.5 Microns 3 3.5 4 4.5 5 Figure 4.3.3-1: Value of the elastic energy density along the AIGaN layer of Transistor A (SiC substrate) under increasing drain-to-source bias at Vgs=OV. The black line indicates the initial state. 6 2 4 6 8 10 Vds /V 12 14 16 18 Figure 4.3.1-2: Percentage change of the peak value of the elastic energy density at the drain edge of the gate as a function of the drain-to-source bias at Vgs=OV (Vds=OV state to high-power state). 10~ 22 -vgs.7V vas tav 2-S 21 -- vgs1V Vers~v -- vg-0oVvS=t8V V--1VVds=18V -vgsm-2VVds=1V -- Vs-VVds13V Vol-O 'v1don1ey -Vgs"O -2.0 2 TransistorA Inverse Piezoelectric Eff VdVe16v Lattice Heating Expansion S -Source Drain-- TransistorA @Vds=18V -*-Change of the Peak Elastic Energy Density Micrns Figure 4.3.1-3: Value of the elastic energy density along the AIGaN layer of Transistor A (SiC substrate) under decreasing gate-to-source bias at Vds=18V. The black line indicates the initial state. 20 -18 -16 -14 -12 -10 -8 Vgs/V -6 -4 .2 0 2 Figure 4.3.1-4: Percentage change of the peak value of the elastic energy density at the drain edge of the gate as a function of the gate-to-source bias at Vds=18V (high-power state to off state). 4.4 Summary In conclusion, we have rigorously derived the piezoelectric-thermal relations in the form of a partial differential equation under the condition of a clamped and free-standing model for AIGaN/GaN HEMTs. By using the data extracted from the previous self-consistent electrothermal simulations, we solved the PDE equation in Matlab and obtained the desired mechanical characteristics-strain, stress and elastic energy density in the GaN-based transistors. In the calculation results, we found that the vertical electrical field and the lattice heating both tensile the lateral strain, but on the other hand, the vertical electrical field compresses, the lattice heating tensiles the vertical strain in the AIGaN layer at the drain edge of the gate, especially under pinch-off condition. This feature explains the mechanisms of crack formation and defects creation in the AIGaN layer observed at the drain of the gate under the off state stress testing of AIGaN/GaN HEMTs. In addition, the calculation of the elastic energy density in devices provides important quantitative results for the prediction of the critical voltage of the reverse-gate-bias degradation and could be further applied to the understing of the fracture mechanisms of AIGaN/GaN HEMTs. CHAPTER 5 5.1 REVERSE-GATE-BIAS RELIABILITY TESTING Introduction As we mentioned in Chapter 1, several authors have observed that significant degradation of AIGaN/GaN HEMTs takes place when the devices are biased in the pinch-off state during the reverse-gate-bias testing at Vds=OV state [24] [25]. In this case, the main failure phenomena observed is a catastrophic increase in the gate leakage for gate voltage beyond a critical voltage [43]. Inthis chapter, we report our work on the use of thermo-reflectance measumrents to study the reverse-gate-bias reliability of GaN-based HEMTs. 5.2 Structure of Tested Transistors The transistors we tested here were fabricated using our reliability testing mask and passivated by A12 0 3 to reach a more reliable performance. The device structure is schematically shown in Figure 5.2-1: Zm Figure 5.2-1 Schematic structure of Transistor C .. .. ...... . ... ......... 5.3 Calibration of Thermo-Reflectance Coefficient Since the surface material of Transistor C is A1 2 03 , the calibration of the thermo-reflectance coefficient of the new material is needed before we can convert the thermo-reflectivity maps into the lattice temperature profiles. 0.00070 - Al203@ T = 300K 0.00055 - 0.00060- 0.00055- 1= (3.94±0.58)x104 0.00050 I 0.2 0.3 0.4 0.5 0.6 0.7 0.8 AT Figure 5.3-1: Variation of the thermo-reflectivity as a function of the variation of the lattice temperature measured on A1203 sample of 300K. The slope of the fitting line is the thermoreflectance coefficient. As in the case of the GaN material, the calibration is fairly linear (error <2% in temperature) and we can approve that the thermo-reflectance coefficient P of A1 203 is also approximately constant over the temperature range of interest (300K to 400K). The analyzed result at 300K is shown in Figure 5.3-1. The thermo-reflectance coefficient is 3.94x10-4 K- for Al20 3 material under the 467nm (blue) LED light. 5.4 DC Measurements of Gate Current Degradation Five AIGaN/GaN HEMTs with the same structure as Transistor C were submitted to a reversebias step stress test, keeping the source and drain grounded so that Vs=0V, Vd=0V and applying a negative voltage to the gate from -1OV to -80V in -1OV steps for 1 minute per step. At the end of each step, device electrical and thermal characteristics were evaluated by DC measurements and thermo-reflectance measurements respectively. Prior to the test, we verified that the five devices, belonging to the same wafer, presented a consistent and reproducible behavior. In this section, the experimental results of the drain and gate current after each step of the stress are demonstrated. As we can see from the figures below, there is a minor degradation for the drain current in the stressed devices but a very steep degradation of the gate current around a critical voltage at Vgs=-40V in good agreement with other authors' observations [25] [43] [44] [45]. 700 0 fresh stressed@Vgs=-80V 00 TransistorCC~: ~~ V s=-1V 100 1-Ves=-3V 100 0 1 2---- 3 4 5 68---- 7 8--9--10 Vds / V Figure 5.4-1: IV curves of the drain current as a function of the drain voltage under various gate bias as for a fresh and a reverse-gate-bias-stressed Transistor C. 10-3 -- Vgs=2VVds=IV -- -Vgs=2V Vds=5V -* - Vgs=-3V Vds=10V - 0--Vgs-3VVds=0V ~-1- 10'4 A 10' T Transistor C 10 10 20 30 40 50 Vsg/V 60 70 80 Figure 5.4-2: Gate current after reverse-gate-bias stress for four different bias conditions in Transistor C. The critical voltage of gate current degradation isfound at Vgs=-40V. 5.5 Thermo-Reflectance Measurements of Degradation This section reports the experimental results for the lattice temperature distribution after each stress step for a typical tested device. Temperature / Temperatue K 3N' ,Orain Stressed @ Vgs=-10V Vds=OV 325 315 Gate 310 Source 5 kn) 295 Figure 5.5-1: Top view of the lattice temperature image of Transistor C (fresh) at Vgs=OV, Vds=1 8V. Figure 5.5-2: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-1 OV Vds=OV) at Vgs=OV, Vds=18V. ...... Tmperature /K 330 Drain Stressed Tmperature /K -330 Vgs=-20V Vds--OV 325 320 315 Gate 310 305 316 G10 305 Source 300 5 ini 295= 295 Figure 5.5-3: Top view of the lattice temperature image Figure 5.5-4: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-20V Vds=OV) at of Transistor C (stressed 1min @Vgs=-30V Vds=OV) at Vgs=OV, Vds=1 8V. Vgs=OV, Vds=1 8V. Temperature / K Temperature/ K 330 330 Drain Stress&d & Vgs=-40V Vds=OV 325 320 315 Gate 310 305 Source 5 pill -------A Iac 296 Figure 5.5-5: Top view of the lattice temperature image Figure 5.5-6: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-40V Vds=OV) at of Transistor C (stressed 1min @Vgs=-50V Vds=OV) at Vgs=OV, Vds=18V. Vgs=OV, Vds=1 8V. Temperature / K 330 Dra in Gate Temperature / K 330 Stressed @ Vgs---60V Vds=OV 325 325 320 320 315 315 310 310 305 Source 300 291= 295 Figure 5.5-7: Top view of the lattice temperature image Figure 5.5-8: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-60V Vds=OV) at of Transistor C (stressed 1min @Vgs=-70V Vds=0V) at Vgs=OV, Vds=18V. Vgs=OV, Vds=18V. emperature / K Temperature / K 330 1330 Drain, Stresse Vgs=42V V 325 320 315 Gate 310 305 Source Pin 295 Figure 5.5-9: Top view of the lattice temperature image Figure 5.5-10: Top view of the lattice temperature of Transistor C (stressed 1min @Vgs=-80V Vds=OV) at image of Transistor C (stressed 1min @ Vgs=-82V Vds=OV) at Vgs=OV, Vds=1 8V. Vgs=OV, Vds=1 8V. As shown in the figures above, we find that before the stress step at Vgs=-80V, the lattice temperature maps for the device are unchanged even after the critical voltage Vgs=-40V for the gate current degradation, however, at and after the stress step at Vgs=-80V, some round 'defects' (the color of those defects has no relation with the color-map of the temperature .......... n:n - .......... because the surface curvatures of them change the thermo-reflectance coefficient) appear at the gate-to-source region. This interesting phenomenon is reported for the first time in this thesis, and its origin will be discussed in details in the next section. 5.6 Discussion In order to explain the change in the thermal map, SEM and AFM images of the stressed device were taken in order to investigate the shape and the scale of those 'defects'. Figure 5.52 shows that those 'defects' are actually 'bumps' on the device surface with -50 nm height and -2 pm width. Figure 5.6-1 Top view SEM image of Transistor C after Figure 5.6-2 3D AFM image of Transistor C after stressed at Vgs=-80V, Vds=OV. stressed at Vgs=-80V, Vds=OV Secondly we took a close look at the thermo-reflectance images around Vgs=-80V. As indicated by the arrows in Figure 5.5-3 below, we find that all the 'defects' are actually created from blue spots (cold area) one step before the stress testing. We believe that the defect density under the blue (cold) regions in the thermo-reflectance images is much higher than in the red (hot) areas because the heat flow is blocked by the defects. The spot '1' in Figure 5.5-3 Aa- Ov4ONJIMI-ft- zkgmqwm - - - - - was still yellow (medium hot) after stressed at Vgs=-70V which means there was still heat flowing under this area, but suddenly at the critical voltage Vgs=-80V, it became a blue (as cold as room temperature) spot as indicated as '2' in Figure 5.5-4 which means defects were created under this region and heat flow was blocked. And then, when further stressed at Vgs=82V, the same spot turned to the obvious 'bump' on the surface as indicated as '3' in Figure 5.5-6 which means the defects were growing fast and even dramatically changing the shape of the surface. These similar processes are observed from spot '4' and '6', which evolve into spots '5' and '7' respectively as indicated by the arrows in the figures below. Tempenature / K 330 Tempefature / K Drain Stressed @ Vgs=-BOV Vds=OV 325 320 315 Gate 310 305 'Ce Figure 5.6-3: Top view of the lattice temperature image Figure 5.6-4: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-70V Vds=OV) at of Transistor C (stressed 1min @Vgs=-80V Vds=OV) at Vgs=OV, Vds=1 8V. Vgs=OV, Vds=1 8V. Temperature I K *Stressd@vs-o d~v 1empMare / D'rai n. K Stressed@ Vgs=-92V Vds=OV ,325 45M, 74 A1 315 GaL'C 310 Source 300 ===295 Figure 5.5-4: Top view of the lattice temperature image Figure 5.5-5: Top view of the lattice temperature image of Transistor C (stressed 1min @Vgs=-80V Vds=OV) at of Transistor C (stressed 1min @Vgs=-82V Vds=OV) at Vgs=OV,Vds=18V. Vgs=OV, Vds=18V. 5.7 Summary Insummary, we have conducted reverse-gate-bias reliability testing on passivated AIGaN/GaN HEMTs, in order to study the effect of the gate current degradation in the thermo-reflectance measurements. Interestingly, surface 'bumps' correlated with the possible defects spots in the lattice temperature maps were found at the critical voltage Vgs=-80V, which is much higher than the critical voltage of the gate current degradation at Vgs=-40V. This result reinforces the conclusion of Chapter 3 that blue spots (cold areas) relate to possible defects under the surface. Thermo-reflectance measurement is a simple and convenient tool to show defects distributions and early breakdown for AIGaN/GaN HEMTs as well. CHAPTER 6.1 6 CONCLUSIONS AND FUTURE WORK Conclusions The basic framework developed in this thesis to study the effect of piezoelectricity in the reliability of GaN-based HEMTs could be summarized in the following flowchart: Reverse-Gate-Bias Reliability Testing Electrical Field Drift-Diffusion Model 0N DC Measurements 00;11 > Critical ITMatlab Piezoelectric- Self-Consistent EectroThermama -The rma Iha Electro Simulations Gate Current Degradation Voltage Programming Strain Elastic Energy Densities Calculations Critical Voltage Thermal-Reflectanc Measuremen Lattice Heating Model Lattice Temperature | > Defects Growing & Surface Bumps Creation Reverse-Gate-Bias Reliability Testing Figure 6.1-1: The thesis flowchart, describing the key models and methods that combine with simulations and measurements for the purpose of degradation testing and reliability prediction of AIGaN/GaN HEMTs. By using the commercial software Silvaco Atlas, we successfully modeled and simulated the electrical and thermal characteristics of the standard AIGaN/GaN HEMTs with good agreement with experimental results. In thermo-reflectance measurements, we found the non-uniformity feature of the temperature distributions along the gate width direction on wafers grown on the Silicon substrate and explained them for the effect of the large defect densities in those devices. In addition, by rigorously deriving the piezoelectric-thermal relations of AIGaN/GaN HEMTs, we found that the strain and elastic energy density peak both peak at the drain edge of the gate under various bias conditions, especially under highly-pinched-off state when nearly 20% changes can be reached. Moreover, surface 'bumps' possibly associated with 73 defects and early breakdown were found in the lattice distribution maps at the critical voltage higher than that of the gate current degradation, which makes thermo-reflectance measurements a potential candidate for a simple and convenient tool to show defects distributions, study degradation mechanisms and predict reliability performance of AIGaN/GaN HEMTs. 6.2 Future Work Future work will be focused on the quantitative analysis needed to find the correlation between the gate current degradation and thermo-reflectance images through the theory of defects formation and critical elastic energy densities in the reverse-gate-bias testing. A more systematic reliability study will be carried out on different sets of transistors. DC, RF, thermo-reflectance and electroluminescence measurements will be conducted after each step stress test. Statistical methods will be used to analyze the correlating patterns among them. 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