United States

Silicon Carbide (SiC) is a wide bandgap semiconductor, which has been widely applied to power electronics due to its excellent properties of wide band gap, high break down voltage and thermal stability. However, defects, such as threading edge dislocations (TEDs), threading screw dislocations (TSDs) and basal plane dislocations (BPDs), can limit the performance of the devices [1,2], so characterization of those defects becomes a critical aspect to improve the quality of 4H-SiC wafers. Synchrotron monochromatic beam X-ray topography (SMBXT) is a powerful technique to characterize the defects with the advantages of large field of view and clear contrast of the defects. SMBXT in 11-28 reflection has been widely used, however, the penetration depth, around 17um [3], appears to be shallow to characterize device with deep PN junction. Therefore, a new reflection with deeper X-ray penetration depth and clear contrast on the defects has been sought for. 22-4 16 reflection, the harmonic reflection of 11-28, shows better contrast on the defects, higher strain sensitivity and deeper X-ray penetration. Contrasts from the same defect of 4H-SiC with 24 um epilayer in 11-28 and 22-4 16 reflections are compared as shown in Fig. 1. From 11-28 SMBXT, BPD segments near the surface of the wafer can be observed, as shown in the blue arrows in Fig 1(a), but contrasts of the segments lying deeper in the crystal are blurred as shown in the green boxes. On the other hand, in 22-4 16 SMBXT (Fig 1(b)), the contrasts of the full BPDs can be clearly seen and the contrasts of BPD segments lying deeper in the crystal are highlighted in green boxes to compare with contrasts in 11-28 reflection. This result also proves that the penetration depth of 22-4 16 SMBXT is deeper than that of 11-28 SMBXT. Previously we have simulated images of defects in 11-28, 0008 and 000 12 using the principle of ray tracing, showing good correlation with the topograph[4,5]. In this paper, we apply the ray tracing principle to simulate defect images in the 22-4 16 topograph and compare and discuss the contrast for the different defect types. Reference: [1] K. Konishi, R. Fujita, Y. Mori and A. Shima, Semiconductor Science and Technology 2018 Vol. 33 Issue 12 [2] W. Gao, G. Yang, Y. Qian, X. Han, C. Cui, Xi. Pi, D. Yang and R. Wang, Frontiers in Materials, Jan 2023, DOI:10.3389/fmats.2023.1022878 [3] Q. Cheng, H. Peng, S. Hu, Z. Chen, Y. Liu, B. Raghothamachar and M. Dudley, Materials Science Forum 1062, 366-370 [4] H. Peng, Z. Chen, Y. Liu, B. Raghothamachar, X. Huang, L. Assoufid and M. Dudley, J. Appl. Crystallogr. 55 (2022) 544-550. [5] H. Peng, Z. Chen, Y. Liu, Q. Cheng, S. Hu, X. Huang, L. Assoufid, B. Raghothamachar and M. Dudley

EMC 2023

Ray Tracing Simulation of Defects of 4H-SiC in 22-4 16 Reflection of Synchrotron Monochromatic Beam X-Ray Topography in Grazing Incident Geometry

ray tracing simulation

4h-sic

defects

technical paper

The Electronic Materials Conference (EMC) is the premier annual forum on the preparation, characterization and use of electronic materials. This year’s event will feature a plenary session, topical sessions, a poster session and more.

EMC is coordinated with the Device Research Conference (DRC). This recognizes the strong interaction between device and electronic materials research and provides fruitful exchange of information between attendees of both Conferences.

The Electronic Materials Conference (EMC) is the premier annual forum on the preparation, characterization and use of electronic materials. 

Nano Fourier Transform InfraRed (nanoFTIR) spectroscopy is a powerful non-destructive characterization technique offering nanoscale spatial resolution combined with spectroscopic information. In this work we apply the combination of nanoFTIR and finite dipole modeling to characterize and identify the polytype of in-grown stacking faults (IGSF) in 4H silicon carbide. The results of stacking fault identification are verified using the established techniques of confocal Raman spectroscopy and ultraviolet photoluminescence spectroscopy. Results from one IGSF consisting of a double layered 3C inclusion will be reported. Results from additional IGSF exhibiting other polytypes are expected as the work continues in upcoming months, with the goal of identifying an IGSF with 8H polytype and extracting the dielectric function using nanoFTIR. 8H stacking faults are common, but the dielectric function of 8H is yet unmeasured due to the lack of commercially available 8H wafers.

Nanoscale Spectroscopy of Extended Defects in 4H Silicon Carbide

Ion implantation is the most useful technology for doping of 4H silicon carbide to fabricate power devices. For n-type doping, nitrogen is the most common element used in device fabrication due to its low atomic mass and proven applicability in epitaxial n-type SiC. Phosphorus can be an alternative to nitrogen (N) for providing a lower sheet resistance, although the research on phosphorus as a dopant is limited [1-3] in range of doping and activation temperatures. A rigorous study comprising different doping concentrations would help to verify the activation percentage and ionization energies and will lead to a better understanding of the properties of dopants other than N, to take advantage of any underlying benefits. In this work, phosphorus is implanted in different concentrations on 150 mm Si-face 4H SiC (0001) of 4 degree off-axis wafers and activated above 1600 oC. To study the electrical characteristics, circular van der Pauw structures were made. Deep p-well implants were performed to isolate the phosphorus doped region from the n-type substrate. Nickel contacts were deposited using evaporation and post-annealed at high temperature to get ohmic contacts. The samples were then placed on a 1cm x 1cm PCB board with 4 contacts at the corners, and wire bonding from sample to board was performed. Following that, 4-point probe resistance and Hall measurements were conducted to obtain resistivity, carrier concentration, and Hall mobility for different doping levels. Thereafter, dopant activation percentage and ionization energy levels are calculated. Figure 1 shows typical IV characteristics of the fabricated van der Pauw samples that indicate linear or ohmic behavior of the contacts. Figure 2 shows the temperature-dependent variation of resistivity for different doping levels. From 150 to 300 K the resistivity drops as temperature increases, while above room temperature a small increase of resistivity can be observed. An increase in the carrier concentration versus temperature is shown in Fig. 3, for doping less than 9x1019 cm-3. The sample with a doping concentration of 9x1019 cm-3 behaves like a semimetal for which the carrier concentration is almost constant with changing temperature. A small upshoot in carrier concentration at very low temperature (~150 K) might be caused either by a change of effective implant thickness with temperature, or p-well dopant freeze out effects underneath the n-wells. Figure 4 shows mobility versus temperature for different Phosphorus implanted concentrations. At lower temperatures mobility drops due to increased ionized impurity scattering. Mobility reaches a peak value near room temperature and drops again as temperature increases due to increased phonon scattering owing to enhanced lattice vibrations. Figure 5 shows the carrier concentrations as modeled in hexagonal and cubic lattice sites (50:50 distribution assumed) with assigned specific ionization energies. For example, for the sample with implanted doping concentration of 4x1018 cm-3, the ionization energies are extracted to be 48 and 110 meV for hexagonal and cubic lattice positions from the model fit. The values of activated dopants are also calculated here from this analysis and plotted as a function of doping concentrations as shown in figure 6. It is clear that the phosphorus activation is well below 100%. The extracted activation percentages and dopant ionization levels will be shown for all samples, and compared to literature values, in the full manuscript. The activation percentages and ionization energies, extracted from the data, will be useful for calibration of Technology Computer Aided Design (TCAD) models for electrical simulations of 4H-SiC based devices. [1] M.A. Capano et al., J. Electron. Mater. 29, 210 (2000). [2] J. Gardner et al., J. Appl. Phys. 83, 5118 (1998). [3] T. Kimoto, J.A. Cooper, Fundamentals of Silicon Carbide Technology (2014).

Study of Dopant Activation and Ionization for Phosphorus in 4H-SiC

Motivation To reduce the device cost, body diode is expected as the freewheeling diode for commercial trench SiC power MOSFETs in the high frequency applications. Therefore, it is necessary to investigate the reliability of body diodes. This study compares the body diode degradation of commercial 1.2 kV planar and trench SiC power MOSFETs from several vendors listed in Table 1. Besides, 1.2 kV planar SiC power MOSFETs are fabricated with the nominal and deep JFET. The deep JFET extends down from the nominal JFET into the drift layer, and part of the additional n+ layer is in contact with p-body. We assume that the deep JFET enhances the recombination of the injected minority carriers from p-body. This leads to the suppression of body degradation by reducing the recombination energy provided to expand SFs. These two different JFET structures are presented in Fig. 1. Results Fig. 2 compares the average degradation ratio of VF, RON, and forward leakage current in the blocking mode (IL) on the commercial 1.2 kV planar SiC power MOSFETs from Vendors E, I, and C. Decline in device performance from body diode degradation is at negligible or acceptable levels for all these three vendors. It can be concluded that body diode degradation is not a big issue in most commercial 1.2 kV planar SiC power MOSFETs. In Fig. 3, commercial trench DUTs from Vendor K have more significant average body diode degradation than planar DUTs. Trench DUTs from Vendor D have no obvious degradation. However, the influence of body diode degradation on IL is not reflected as expected. This may be due to the fact that devices are breaking down in the termination area where no SFs exist, as opposed to the active area. As shown in Fig. 4, 7 of 10 DUTs from Vendor K have reached the degradation criterion while there’s no significant body diode degradation in 8 DUTs, apart from the 2 dead devices, for Vendor D. This can be explained in Fig. 5 that the deep p+ contact by the Al implantation with high dose and energy is required to shield the electric-field-crowded corner of the trench gate, which creates many BPDs around the p+ contact in the trench structure from Vendor K. Although the p+ contact with the heavy dose is still needed for Vendor D, it is implanted after the dummy trench formed by RIE. That means the p+ contact can be shallow which significantly reduces the new BPDs. In the planar structure, high density of new BPDs around the implanted regions is hard to create because of light-dose and shallow p-type contact, as well as many improved designs and processes that have already minimized the BPDs arising from the SiC substrate wafer and epitaxial growth. In addition, Vendor D not only has the Gen 3 trench structure mentioned above, but also has the Gen 4 trench structure as shown in Fig. 6. In the Gen 4 trench structure, the Al implantation with the high energy and dose for the deep p+ contact is performed before the RIE for the trench dummy. Therefore, this new trench structure is expected to have significant body diode degradation as that of Vendor K. The body diode degradation test on the Gen 4 DUTs from Vendor D is still in progress. Furthermore, Fig. 7 compares the body diode degradation of the fabricated 1.2 kV SiC power MOSFETs with the nominal and deep JFET. It can be observed that there is increasing average body diode degradation in the DUTs with the nominal JFET during the stress. However, for the DUTs with the deep JFET under the same process, there is no average body diode degradation during the stress. It is also reflected that the breakdown voltage of the DUTs with the nominal JFET decreases due to the increasing leakage current while there is no variation for the DUTs with the deep JFET. This confirms the assumption that body diode degradation in commercial 1.2 kV SiC power MOSFETs, especially in the trench devices, is mainly caused by the new BPDs around the p-type contacts introduced by the deep Al implantation with heavy dose.

A Comparison of Body Diode Degradation in Commercial 1.2 kV SiC Power MOSFETs with the Planar and Trench Structure

Generation of basal plane dislocations (BPDs) in 4H-silicon carbide (SiC) epitaxial layers due to ion implantation was reported by Stahlbush et. al. [1]. These BPDs formed loops that were generated at the epitaxial layer surface within the implanted layer and propagated towards the substrate interface. Such BPD generation was observed when high dosage Al ion implantation was carried out at room temperature (RT) for typical contact formation. With recent advances in device processing, several of these newly generated BPDs have been mitigated either by high temperature (HT) ion implantation or by other processing techniques such as post implant oxidation [2]. It is, however, desirable to perform ion implantation at RT to reduce high temperature fabrication steps, which could affect wafer yield due to less thermal induced stress in the wafer. It is also unclear in device layers with differently doped regions if the BPDs would result in stacking fault (SF) formation and if the typical carrier injection conditions would cause SF expansion. In this work, we investigate SF expansion from potential BPDs generated by ion implantation in SiC epitaxial layers that had both RT and HT ion implantation and compare their robustness using high carrier injection using high intensity ultraviolet (UV) laser excitation. For this work, MOSFET device structure with 30 mm drift layers were fully fabricated on 4 commercial 150 mm diameter SiC wafers at a commercial foundry. Two of the wafers had a RT implant for the high Al dose contact layer and two remaining wafers had a HT implant performed at approximately 600 oC. Several of the device dies were removed from each of the four wafers and their metal layers were stripped to observe the generation of defects. UV photoluminescence (UVPL) imaging using a 355nm laser and a microscopy setup was performed with typical (10-20 W/cm2) excitation power on all the 4 samples. This was followed by high intensity (500 W/cm2) UV carrier injection. Sequence of images were collected to study progression of SF formation. The UVPL images obtained using typical excitation power did not introduce any BPDs in either the RT or the HT implanted samples even after exposure for several minutes. Upon UV excitation at 500 W/cm2, SF expansion from BPDs were observed in the RT implanted samples near the edge of the termination regions and not in the active areas within 8 secs. UV excitation generates carriers with an exponential depth decay uniformly across the device region, which is different from current injection that depends on background doping. Hence, in highly doped regions, UV excitation simulates significantly higher minority carrier generation responsible for SF generation compared to current injection. A comparison of UV excitation power with current injection conditions will be presented. The active device region did not show SF expansion, which is likely due to fast recombination of electrons from the implanted region due to depletion in the p-well. Details of the mechanisms will be presented. In the HT implanted samples, no SFs were observed even after 96 secs of high intensity UV exposure, indicated no generation of new BPDs. Even though SF expansion was not observed in active regions of the RT samples, BPD are likely formed in the contact layers and pose a reliability issue for long term device operation, especially if surge current conditions are expected during switching. [1] R. E. Stahlbush, N. A. Mahadik, Q. Zhang, et. al., Mater. Sci. Forum 821-823, 389 (2015) [2] Y. Bu, H. Yoshimoto, N. Watanabe, et. al., J. Appl. Phys., 122, 244504 (2017) Acknowledgement: Author Kallon’s research was sponsored by the Office of Naval Research NREIP program.

Reliability of Room Temperature vs High Temperature Implantation in 3.3kV SiC MOSFETs

Molecular electronics are being developed as materials for light-harvesters and -emitters, sensors, and quantum technology. The themes for optimizing these systems are miniaturization and improved precision, which increasingly moves these materials into the quantum-mechanical regime. Natural systems like photosynthetic pigment-protein complexes have shown that vast improvements to functional bottlenecks like energy-transport can be achieved, if the structural and energetic properties are finely controlled. In that spirit, we are developing modular molecular networks whose structures are controlled by DNA scaffolds. This approach controls the network’s structural, energetic, and dynamic properties. However, this increased control presents new needs and challenges. We must know what the ideal parameters are for optimal function. In turn, that optimization requires a better understanding of the molecular-scale characteristics of the systems. Another challenge is that these characteristics often include many degrees of freedom, especially for large chemical networks, so an approach must be developed to treat large amounts of data efficiently, yet thoroughly. Here, we describe approaches to address these challenges. By combining machine-learning tools with experimental spectroscopies and computational models (Figure 1), we can simultaneously understand and map the sample characteristics on the molecular scale, the energy transport characteristics on the mesoscale, and the material performance on the bulk scale. We will discuss how we have used these tools to predicted optimal system configurations for energy-transport, and how they reveal the interchromophore effects in chromophore arrays.

Understanding Electronic Energy Transport in DNA-Scaffolded Molecular Networks Using Machine-Learning Methods

Organic molecules, such as pentacene, rubrene and phthalocyanine are at the forefront of materials research, due to their desired electric, excitonic and mechanical properties. They represent the feasible alternative to traditional silicon-based semiconductor applications for flexible electronics platforms, where materials in flexible devices will experience complex strain environment. Octabutoxy phthalocyanine (H2-OBPc) is a soluble derivative of the Phthalocyanine (Pc). It has π-conjugated systems and large directional intermolecular interactions, which allow the formation of molecular crystal with well-defined structure like J-aggregate, where molecules are stacked in a head-to-tail fashion (Fig.1a). 1, 2 In this quasi one-dimension system, the Frenkel exciton can couple with lattice and intramolecular vibrations to form exciton-polarons which are delocalized along the molecular aggregates. The formation of these one-dimensional delocalized exciton-polaron states grants H2-OBPc the potential for efficient excitation energy transport in the coherent exciton regime. 3-6 In this work, H2-OBPc polycrystalline thin films were prepared using a solution-based pen-writing deposition technique. These ordered thin films with macroscopic grain size (Fig.1b, millimeter scale) uniquely offer the opportunity to spatially explore optical and excitonic properties within a single crystalline grain, free from the influence of grain boundaries or static disorder (Fig.1b). Temperature-dependent absorption and photoluminescence (PL) experiment points to the existence of red-shifted bandgap when temperature T < 175 K (Fig.2c and d). This new bandgap at low temperature is the result of the formation of exciton-polaron states, where the molecular Frenkel excitons couple with intermolecular low energy phonon modes (i.e. dynamic disorder fluctuations ), leading to the wavefunction spreading over the π-stacked molecular chain (Fig.1a). These delocalized exciton-polaron states have robust emission properties and they are potentially coherent. 6 The critical role played by low-energy phonons (25-300 cm-1) 7 in the formation of delocalized, 1D coherent exciton-polaron states is explored using an externally applied uniaxial mechanical strain (example of the tensile strain geometry is shown in Fig.2a). Strain-dependent absorption (Fig.2b), PL microscopy (Fig.2c), and confocal Raman measurements (Fig2.e) reveal the strain-induced softening (red shift) of the phonon modes favors the survival of the coherent exciton-polaron states at room temperature (A2 peak in Fig.2b and P2 peak in Fig.2c). Remarkably, an 80% enhancement in PL intensity is observed with a uniaxial tensile strain of 4.7% applied at room temperature (Fig.2c), which is equivalent to lowering the temperature to 200K for the unstrained film. 8 Time-resolved transient absorption (TA) spectroscopy confirms the behavior of the exciton-polaron state as a function of strain. Reference (1) Rawat, N.; Pan, Z.; Manning, L. W.; Lamarche, C. J.; Cour, I.; Headrick, R. L.; Waterman, R.; Woll, A. R.; Furis, M. I. J. Phys. Chem. lett. 2015, 6, (10), 1834-1840. (2) Manning, L. W.; Rawat, N.; Lamarche, C.; Waterman, R.; Headrick, R. L.; Furis, M. J. Phys. Chem. C 2016, 120, (22), 11966-11976. (3) Ghosh, R.; Spano, F. C. Acc. Chem. Res. 2020, 53, (10), 2201-2211. (4) Spano, F. C. Acc. Chem. Res. 2010, 43, (3), 429-439. (5) Yamagata, H.; Spano, F. C. J. Phys. Chem. lett. 2014, 5, (3), 622-632. (6) Liang, L.; Burrill, K.; Furis, M. I. J. Phys. Chem. C 2021, 125, (51), 27966-27974. (7) Fornari, R. P.; Aragó, J.; Troisi, A. J. Phys. Chem. C 2016, 120, (15), 7987-7996. (8) Liang, L.; Czar, K.; Furis, M. I. J. Phys. Chem. C 2022, 126, (20), 8889-8896.

Strain-Enhanced Formation of 1D Coherent Exciton-Polaron States in Small Molecule Semiconductors

There have been studies of understanding and controlling the charge transport through molecular junction wince it gives fundamental grounds that helps to gain a novel idea to realize numerous potential molecular functional devices. [1,2] There are some key factors considered in molecular charge transport, such as molecular barrier which is directly related to molecular orbital levels, coupling strength, asymmetric factor, and molecular configuration and conformation. Much research has been reported to obtain deeper insights of such key factors under certain controlled conductions with the effect of the external stimuli applied on the molecular junction such as light irradiation [3], electrochemical gating [4], electrical field [5], and mechanical stress such by tip loading force [6]. Molecular heterojunction with two-dimensional (2D) semiconductor provides various key factors for the charge transport through the heterojunction; however, the effect of molecular tilt configuration on the molecular heterojunction have never been studied. Here, we present the effect of molecular tilt configuration on the molecule/mono-layer (1L) 2D semiconductor heterojunction by tip loading force with conductive atomic force microscopy (C-AFM) technique. With various tip loading force (1-30 nN), the molecular tilt configuration affects differently for the three different interfaces in Au/molecule/1L-2D semiconductor/Au heterojunction that the transition voltage spectroscopy (TVS), which is a conventional tool to analyze charge transport through molecular junction, rectification ratio (RR), non-linearity (NL) and possible array size are demonstrated. Molecule/2D semiconductor heterojunction system has been reported as molecular diode (with RR) and selector (with NL) and it is a novel platform owning so much various potential in, that understanding the charge transport by the effect of external stress on the heterojunction will help developing such future molecular scale functional devices. [1] L. A. Bumm, J. J. Arnold, M. T. Cygan, T. D. Dunbar, T. P. Burgin, L. Jones, D. L. Allara, J. M. Tour, P. S. Weiss, Science 271, 1705 (1996),. [2] H. Song, Y. Kim, Y. H. Jang, H. Jeong, M. A. Reed, T. Lee, Nature 462, 1039 (2009). [3] G. Reecgt, C. Lotze, D. Sysoiev, T. Huhn, K. J. Franke, ACS Nano 10, 10555 (2016). [4] R. A. Wong, Y. Yokta, M. Wakisaka, J. Inukai, Y. Kim, Nat. Commun. 11, 4194 (2020). [5] J. Shin, S. Yang, Y. Jang, J. S. Eo, T.-W. Kim, T. Lee, C.-H. Lee, G. Wang, Nat. Commun. 11, 1 (2020). [6] G. Wang, T. -W. Kim, G. Jo, T. Lee, J. Am. Chem. Soc. 131, 5980 (2009).

Effect of Molecular Tilt Configuration in Molecular Heterojunction with Two-Dimensional Semiconductor

Many semiconductor devices (e.g., light emitters and photovoltaics) utilize heterojunctions of doped and undoped layers or depend on gradients of electronic doping to control charge transport. Doping of conjugated polymers requires the introduction of small molecules dopants which undergo charge transfer reactions with the polymer. The rate of the doping reaction and diffusion of the dopant controls the overall doping level. Conjugated polymers can be electrically doped by strong acids, but the details of the reaction mechanism and subsequent stability are not understood. Here, we show a clear kinetic isotope effect in the doping of thin films of poly(3-hexylthiophene) (P3HT) by bis(trifluoromethane)sulfonimide (HTFSI) from solution indicating that this doping process is limited by proton transfer to the polymer. The subsequent charge transfer reaction occurs rapidly between polymer segments in the solid state, thus circumventing the need to match redox potentials of dopants and conjugated polymers. Dynamic secondary ion mass spectrometry (DSIMS) of doped films show that H/D is retained in doped films after the doping process. Complementary X-ray photoelectron spectroscopy and DSIMS depth profiling of dopant concentrations show definitive evidence of enrichment at the P3HT surface. These surface-limited concentration profiles suggest that diffusivity of dopants vary inversely with dopant concentration due to doping-induced changes to the structure of the conjugated polymer.

Surface-Confined Brønsted Acidic Doping of Conjugated Polymers Thin Films

The paper reports on a novel process flow to manufacture conductive organic electrodes from highly conductive doped PEDOT:PSS polymer films that can be patterned and display good adhesion to oxidized Si wafers as well as to flexible substrates, such as Mylar. It is shown that multiple depositions of PEDOT:PSS increase the electrical conductivity by more than two orders of magnitude without increasing the film thickness of PEDOT:PSS significantly. An exponential dependence between sheet resistance and the number of PEDOT:PSS coatings is found. Additional coatings, in excess of 6 coatings provide diminishing returns to the lowering of the sheet resistance. The dependence of the sheet resistance Rsq(n) as function of the number of PEDOT:PSS coatings, n, can be described by the formula Rsq(n)=230×exp[-(n-1)×1.28] kΩ. The multiple coating methods can be further optimized by selecting a low spinning speed (e.g. 1500 rpm) for the initial coatings and a high spinning speed (e.g. 3000 rpm) for the final coatings. The reason for the decrease in the sheet resistance is the densification of the conductive PEDOT ribbons at the bottom part of the PEDOT:PSS layer. The electrical conductivity of PEDOT:PSS can be increased by another two orders of magnitude by doping it with Cu nanoparticles (Cu NP) when coated on the surface of a soft-baked PEDOT:PSS film. However, if Cu NP are dispersed in the aqueous solution of PEDOT:PSS then the impact on the sheet resistance is nil. It is found that both kinds of conductivity enhancement are not additive. The doping with Cu nanoparticles is desirable, as it provides the surface of an organic electrode with readily ionized copper ions useful for several applications including Cu filament formation in organic switching layers of a resistive RAM (ReRAM) memory cell. Adhesion of PEDOT:PSS to oxidized Si wafers and to BoPET (Mylar) has been ensured by applying an oxygen plasma cleaning step prior to spin coating. The manufactured high conductivity PEDOT:PSS film can be patterned using a sacrificial metal layer with subsequent etching of PEDOT:PSS in oxygen plasma, followed by the removal of the patterned segments of the sacrificial metal layer in an aqueous acid solution on both Si wafers and flexible Mylar substrates. A single PEDOT:PSS layer has a thickness of around 60 nm depending on the spinning speed and has sheet resistance (Rsq) of 230 kΩ. The same deposition applied 6 times results in a PEDOT:PSS layer of 90 nm thickness (instead of 6×60 nm=360 nm) and Rsq=980 Ω. A surface doping of 1xPEDOT:PSS with Cu NP lowers the sheet resistance from 230 kΩ to 60 kΩ, whereas in the case of multiple coatings, the 6xPEDOT:PSS with the same Cu doping lowers the Rsq from 980 Ω to 6.2 Ω. Thus, with reference to one PEDOT:PSS layer, the sheet resistance has been reduced by a factor of 4×104. The methods described above can be further combined with the methods of in situ doping of PEDOT:PSS with inert metal NP such as Ag and Au NP, that are largely immune to the oxidation reactions in the aqueous solutions, and with acid treatment such as nitric or phosphoric acid. It has been found that all the various methods to increase the conductivity mentioned above are not additive and, in some cases, work at cross-purposes with one another. Therefore, a tailored optimum combination of the available methods requires a detailed understanding of their respective mechanisms. Careful morphological analysis performed by dint of optical microscope picture and surface roughness plots by AFM reveals a close interplay between the thickness of the PEDOT:PSS film, the density of the PEDOT:PSS particles - here controlled by the multiple coatings -, and the size of the Cu NP. The size of Cu NP should be smaller than the film thickness, and the density of PEDOT:PSS particle should be neither too small nor too high to accommodate the Cu NP in the PSS spaces between the conductive PEDOT ribbons to achieve the lowest sheet resistance.

Manufacturing of Highly Conductive Organic PEDOT:PSS Films for Electronic Devices

Electrocorticography (ECoG) is a critically important neuroscientific tool for recording neural activity in the cerebral cortex. Advances in recent years have produced high-resolution ECoG arrays, which have enabled brain-machine interface (BMI) applications such as speech and motor intention decoding systems. Alternatively, cortical activity can be studied using optical tools such as genetically encoded calcium indicators (GECIs) and optogenetics. Optical access to the brain is typically achieved with a small craniotomy covered by a transparent window. Electrophysiology and optical imaging provide complementary neural sensing capabilities: electrophysiological recordings have high temporal resolution, while optical imaging allows recording of genetically-defined populations at high spatial resolution. Combining these two modalities for simultaneous large-scale, multimodal sensing of neural activity across multiple brain regions can be very powerful. To this end, many research groups have developed transparent ECoG arrays that can be used simultaneously with optical recording methods in small rodents and nonhuman primates. These devices are made possible by using transparent conductive materials such as graphene or indium tin oxide (ITO). Alternatively, poly(3,4-ethylenedioxythiophene) polystyrene sulfonate (PEDOT:PSS) is a biocompatible transparent organic conductor which is routinely used to coat chronic neural interfaces in order reduce the interfacial impedance of the contact site. We have developed inkjet-printed transparent PEDOT:PSS microelectrodes which use a novel ring-shaped geometry to reduce interfacial impedance and improve charge injection. [1] This is accomplished by taking advantage of the volumetric capacitance in PEDOT:PSS. Ring-shaped microelectrodes with diameters ranging from 300 µm to 550 µm were fabricated by inkjet-printing PEDOT:PSS, encapsulating with Parylene C, and then exposing a contact site that is much smaller than the microelectrode outer diameter. This unique structure allowed the encapsulated portion of the microelectrode volume surrounding the contact site to participate in signal transduction, which reduced impedance and enhanced charge storage capacity. For the same size contact site, increasing the outer diameter of the encapsulated electrode from 300 to 550 μm reduced the impedance from 294 ± 21 to 98 ± 2kΩ, respectively, at 1 Hz. Similarly, the charge storage capacity was enhanced from 6 to 21 mC cm-2. The PEDOT:PSS microelectrodes provide a low-haze, high-transmittance optical interface, demonstrating their suitability for optical neuroscience applications. They remained functional after a million 1 V stimulation cycles, up to 600 μA of stimulation current, and more than 1000 mechanical bending cycles. We have integrated these inkjet-printed PEDOT:PSS electrodes into transparent cranial windows for multi-modal recording of activity from the cortex.[2] Implanted on transgenic mice expressing the Calcium (Ca2+) indicator GCaMP6f in excitatory neurons, these “eSee-Shells” provide a robust opto-electrophysiological interface for over 100 days. eSee-Shells enable simultaneous mesoscale Ca2+ imaging and electrocorticography acquisition from multiple brain regions covering 45 mm2 of cortex under anesthesia and in awake animals. These eSee-Shells allow either mesoscale imaging across the entire field of view (FOV) or random-access cellular level imaging of small FOVs throughout ≈45 mm2 of the cerebral cortex, an area that is an order of magnitude larger than previous transparent ECoG electrode arrays. [1] P. D. Donaldson and S. L. Swisher, Physica Status Solidi (a) 2022. [2] P. D. Donaldson et al., Adv. Healthcare Mater. 2022.

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Ray Tracing Simulation of Defects of 4H-SiC in 22-4 16 Reflection of Synchrotron Monochromatic Beam X-Ray Topography in Grazing Incident Geometry

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Nanoscale Spectroscopy of Extended Defects in 4H Silicon Carbide

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