An organic liquid electrolyte gives good wetting and relatively high room-temperature ionic conductivity. A dissolved lithium salt supplies mobile ions, while a suitable solvent mixture supports operation beyond the narrow water-stability window. The liquid infiltrates a porous electrode and accommodates modest dimensional changes, helping lower interfacial resistance.

The disadvantages include flammability or combustibility, leakage, solvent volatility and interfacial decomposition outside the stable potential range. A solid electrolyte interphase can passivate the negative electrode, but its formation consumes lithium and electrolyte and its continued growth increases resistance. An electronically insulating separator remains essential. Ionic conductivity alone does not guarantee safety or a large lithium-ion transference number, and low temperature can sharply increase resistance.

Use high-resolution transmission electron microscopy with a coherent, well-aligned beam and an objective aperture admitting the direct beam and the spatial frequencies required at the interface. Orient a crystalline region near a suitable zone axis so that useful lattice fringes are excited; minimize drift, vibration and astigmatism. Choose defocus and aberration correction to transfer the target frequencies, rather than treating the image as a direct map of atoms at arbitrary defocus.

An aberration-corrected scanning transmission electron microscopy probe with high-angle annular dark-field imaging can instead resolve an interface with more directly interpretable atomic-number contrast. A nominal $150\mathrm{nm}$ thickness may be too great for clean atomic-resolution interpretation: thin the interface further if necessary, finish focused ion beam milling at lower ion energy to reduce damaged surface layers, and check for curtaining and implantation. The best mode depends on crystallinity and damage sensitivity; an amorphous interface calls for resolving its boundary and composition rather than inventing lattice fringes.

Use a low-dose, dose-efficient acquisition rather than assuming that a lower accelerating voltage is always gentler. Focus and align on a sacrificial neighbouring region, blank the beam between exposures, illuminate only when recording and use an efficient detector. A broad, low-current-density transmission electron microscopy exposure can avoid a high instantaneous local dose; scanning can also work if probe current, dwell time and repeated visits are controlled.

Radiolysis starts with inelastic scattering and ionization. For an appropriate thin specimen, increasing the electron energy can reduce the inelastic interaction probability and energy deposition per incident electron, so a relatively high voltage can help. However, increasing voltage can also activate knock-on displacement. The optimum therefore depends on the material and the amount of useful information obtained per damaging event; $150\mathrm{nm}$ alone does not determine it. Cooling may reduce diffusion-driven chemical changes but does not eliminate primary ionization. An experimental study of nonbiological layered polymer films explicitly found that the voltage choice must balance damage with image signal.^[ref]

Use conventional bright-field transmission electron microscopy, with nearly parallel illumination, a suitably small objective aperture and low magnification covering the whole cross-section. More strongly scattering material sends more intensity outside the selected central beam and therefore looks darker. Tilt crystalline layers away from strong Bragg diffraction conditions to reduce diffraction contrast, and use a near-focus image so that electron phase contrast does not dominate.

The nominally uniform $150\mathrm{nm}$ thickness helps separate composition from thickness variations, but does not make the contrast purely compositional: density, atomic number and multiple scattering still matter. Choose an accelerating voltage sufficient to transmit this thickness, commonly $200$–$300\mathrm{kV}$ for a robust inorganic film, subject to its damage limit. High-angle annular dark-field imaging in scanning transmission electron microscopy is a useful alternative for approximately monotonic mass-thickness contrast, but is a different acquisition mode and still requires thickness and detector-angle control.

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The transport mean free path is $\ell =v_F{\tau }_{\mathrm{tr}}$, while $\mu =e{\tau }_{\mathrm{tr}}/m^{\ast }$. Eliminating the scattering time gives $\ell =\mu \hslash k_F/e$. The usual ballistic focusing mobility criterion $\ell \gtrsim L$ therefore givesA more geometrically faithful first-peak survival criterion uses the semicircular path length $s=\pi L/2$, giving $\mu \gtrsim 17.4{\mathrm{m}}^2{\mathrm{V}}^{-1}{\mathrm{s}}^{-1}$. There is no sharp universal visibility threshold: clearly resolved peaks favour $\ell \gg s$, small aperture broadening and specular reflection. The mobility inferred in part (ii) corresponds to $\ell \simeq 314\mu \mathrm{m}$, comfortably above both estimates. Higher-order peaks can still be reduced by boundary roughness even when bulk mobility is high.

Substituting $r_c=\hslash k_F/(e|B|)$ into $L=2j{r}_c$ givesUsing the density-derived Fermi wave vector gives the first three peak magnitudesThe equally spaced sequence follows from the number of reflected half-orbits, not from successive quantum Hall fillings. The field polarity selecting a given injector–collector orientation follows from the Lorentz force direction.

This is transverse magnetic focusing. The depleted gates form reflecting boundaries and two constrictions. A narrow quantum point contact collimates carriers into cyclotron trajectories with cyclotron radius $r_c=m^{\ast }{v}_F/(e|B|)=\hslash k_F/(e|B|)$. When an integer number of semicircular skipping arcs links the two openings, the collector couples particularly strongly to the injector population. A floating voltage contact then changes its electrochemical potential to satisfy zero net current, producing a peak in the measured nonlocal voltage. Sweeping the field changes the arc diameter, moving the focused population into or away from the collector.

The connection condition is $L=2j{r}_c$ for integer $j\ge 1$, with the higher orders requiring specular reflections. The effect needs ballistic electron transport, sufficiently narrow openings and a smooth boundary. Electron phase coherence can add interference structure, but the basic geometrical focusing condition is semiclassical.^[ref]

There is a polarity qualification in the printed geometry. The electron charge is negative: for a field out of the page, an electron launched upward through the left opening bends left, not toward the right opening. A direct left-opening-to-right-opening focusing path in the upper region therefore requires the field into the page; the printed outward field supports the reverse connection. Reversing conventional current reverses the occupation perturbation and voltage sign, but does not reverse the curvature of an individual electron. Thus the standard injector-to-collector explanation describes the focusing mechanism, while the asserted signed voltage increase requires a consistent field/lead convention. The calculated results below are peak-field magnitudes; taking outward field positive gives negative fields for direct left-to-right electron injection.

For the silver nanowire network, synthesize or source long, narrow wires, remove excess ligand without causing aggregation, formulate a stable coating ink and coat the flexible web by a scalable method such as slot-die coating or gravure printing. Dry below the substrate's damage temperature, then press or locally weld junctions and embed or cap the network if required. Define 100 µm stripes by masked coating, a printing-compatible patterned wetting layer, or post-coating laser ablation; provide robust end contacts and remove stray bridges between adjacent stripes. Roll processing offers throughput, but coffee-ring effect, wire alignment, random weak links and ablation damage require inline optical/electrical inspection. Verify that the local junction treatment improves resistance without simply darkening the whole film.

For the silver nanoparticle-derived grid, use a repeatable nanoimprint lithography to form a fine mesh inside the outer 25 mm by 100 µm stripe pattern. Fill the channels with a silver nanoparticle ink, remove excess from the transparent openings, and consolidate the metal by substrate-compatible chemical, photonic or low-temperature thermal sintering. Transfer or embed the grid into the polymer surface and add electrical pads. The quantitative design in part (b) sets target pitch, line width and thickness; the large-scale process must maintain those dimensions and a continuous metal cross section. A master enables repeated replication and deterministic open area, but tooling cost, incomplete filling, residual metal in windows, shrinkage cracks, imperfect sintering and adhesion are important limitations. Test the finished patterned stripes, rather than relying on a large unpatterned test coupon alone.

Three credible architectures are a welded silver nanowire network; a thin silver nanowire network with a conducting polymer overcoat; and a nanocrystalline silver grid formed from nanoparticle ink. Silver provides low intrinsic resistivity. A sparse long-wire network can be both flexible and highly transmitting if its junctions are well connected. A thin, optically weak conducting polymer overcoat can bridge junctions and smooth the surface, provided its added absorption and moisture sensitivity are controlled. A fine grid offers a more directly designed optical/electrical trade-off and does not rely on operating near random percolation.

For a quantitative grid feasibility screen, take pitch $p=5\mu \mathrm{m}$, line width $w=100\mathrm{nm}$ and metal thickness $t=200\mathrm{nm}$. An opaque-line square-grid estimate gives $T_{\mathrm{grid}}\simeq (1-w/p{)}^2=0.9604$. With a transmitting polymer substrate of 0.95, the combined estimate is 0.912. The sheet resistance is approximately $R_{\square }={\rho }_{\mathrm{eff}}p/(wt)$. Even an effective silver resistivity four times $1.6\times 10^{-8}\Omega \mathrm{m}$ gives $R_{\square }\simeq 16\Omega$, with a coating thinner than 400 nm. There are about 20 mesh periods across the stripe, making the finite-width design more credible than a pitch comparable with its whole width.

These are feasible material/process choices, not guaranteed specifications for every film carrying those names. For the two nanowire architectures, choose wire dimensions, loading and junction treatment to pass the same finished-stripe measurements; the hybrid's optical budget must include its overcoat. Measure transmission at 550 nm with its reference stated, sheet resistance, profile thickness, bend-cycle stability and pattern continuity. Bare nanotube or graphene networks should not be assumed to meet this demanding resistance–transmission combination without additional metallic conduction or other demonstrated improvement.

A transparent metallic network must span the patterned electrode with many redundant current paths while obscuring little area. For random rods, number density times squared wire length is a useful percolation measure; greater aspect ratio generally reaches a connected network at lower coverage. Conductivity also depends on intrinsic metal resistivity, wire cross section, orientation, length distribution, wire–wire contact resistance and the number of junctions along each spanning path. Insulating capping layers can make nanowire junction resistance dominate even when the individual wires are excellent conductors.

Near the connectivity threshold, small density changes or wire breaks produce large resistance changes. For a narrow stripe, finite-size effects and orientation matter: a macroscopic sheet-average percolation result does not ensure a reliable 100 µm-wide path. Optical performance depends on coverage, metal extinction, wire diameter, aggregation, optical haze, substrate transmission and any binder. Increasing wire density lowers resistance but usually lowers transmission. Welding, pressing or suitable embedding can improve contacts with less additional optical coverage than simply adding metal.^[ref]

The stripe has $L/W=250$ squares, so its end-to-end resistance is $R=250R_{\square }$; the stated sheet-resistance limit requires a stripe resistance below 5 kΩ, not 20 Ω. The sketch below separates sparse connectivity, redundant paths and junction quality.

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With planar anchoring on the cylindrical side wall, uniform axial alignment $\mathbf{n}=\hat{\mathbf{z}}$ is a simple defect-free profile. The axial direction is tangent at every wall point, so it satisfies the lateral boundary everywhere without elastic distortion.

This assumes degenerate planar anchoring, or an azimuthal preference compatible with axial alignment. End constraints, selected circumferential anchoring or imposed twist can favor another state. planar anchoring alone does not require a circumferential vortex. The original axial-section sketch shows the uniform axial option.

Choose an asymmetric diblock copolymer in a cylinder-forming regime: minority cylinders lie in a continuous majority matrix. Form and anneal a film to develop microphase separation, control substrate and top-surface preferences or apply a suitable field to orient cylinders normal to the film, then selectively remove the minority phase. The retained majority matrix becomes the porous support. Infiltrate the channels with liquid crystal. The majority phase forms the channel walls; removing that continuous matrix would not generally leave a continuous nanoporous membrane.

With homeotropic anchoring, the director is radial at a cylindrical side wall. A strictly transverse radial texture has a line core, but an escaped radial texture can avoid it:The director turns axially at the center and is normal to the wall at radius $a$. The original axial-section sketch shows this three-dimensional escape. End conditions, channel dimensions and anchoring strength determine whether escape or a defect-containing profile is favored.

A sphere with degenerate planar anchoring can have a bipolar texture with two surface boojums at opposite poles along the far-field axis. Surface director lines remain tangent, curve between the polar cores and relax toward uniform alignment far away. The original cross-section shows both cores.

A globally regular tangent orientation field cannot cover a sphere; the associated surface winding indices sum to its Euler characteristic, two. These are surface defects, not two arbitrarily placed bulk hedgehogs. Finite anchoring allows deviations near the cores, while an azimuth-selective coating could favor a different texture.

Strong homeotropic anchoring requires radial orientation just outside a sphere, while the remote director is uniform. A plausible dipolar texture contains a compensating hyperbolic hedgehog defect on one side. The particle's radial boundary has charge $+1$ under a consistent convention, balanced by an exterior point defect of charge $-1$ so the far field is uniform. The original cross-section depicts this configuration.

An alternative has an equatorial Saturn-ring defect. Its local disclination winding is half-integer; that local winding is not itself the net three-dimensional compensating charge. Particle size, elastic constants, confinement and anchoring strength select between configurations. The elastic theory explicitly compares dipolar, Saturn-ring and surface-ring states.^[ref]