USING PROTEIN NANOWIRES

This application claims priority to and the benefit of US Provisional

Applications 62/738,320, filed September 28, 2018 and 62/835,023, filed April 17, 2019, which are both incorporated herein by reference in their entirety.

Technical Field

The present invention relates generally to the production of electric power, and more particularly, to devices fabricated with conductive protein nanowires or nanowire composites that generate electric power from ambient atmospheric moisture and methods of using such devices to generate continuous electric power.

Background

Sustainable sources of power are required to mitigate environmental threats associated with fossil fuels. Harvesting energy from the environment has shown growing potential in providing clean energy and supporting self-sustained systems. Known technologies include solar cells, wind turbines, thermoelectric devices, and mechanical generators. Each of these technologies is constrained by specific environmental conditions such as light intensity, wind speed, thermal gradient, and vibration density, and hence are limited in providing continuous and ubiquitous energy.

Atmospheric moisture, which has elevated free energy compared to liquid water, is a diffusive and ubiquitous energy source. For example, even the Sahara Desert has an average relative humidity (RH) around 25%. The earth’s

atmosphere, in fact, contains an amount of water equivalent to 10% of total volume of freshwater lakes in the world. When condensed to liquid water, this atmospheric supply of water can release nearly 10 ¹⁸ kJ of energy, which is an order of magnitude larger than annual global electricity consumption (which is around 10 ¹⁶ - 10 ¹⁷ kJ). This potential has aroused recent interest in developing methods for harvesting the energy available in atmospheric moisture. Two main strategies have generally been adopted.

The first strategy relies on a moisture gradient near sources of liquid water to drive micro/nanofluidic water transport in a thin film to induce charge imbalance and transport for electric output. This technology, however, is restricted to environments where there is an existing liquid water source (e.g., near a body of water or water surface) and may be difficult to scale up.

The second strategy relies on an engineered gradient in surface functional groups in carbon material (e.g., carboxyl group) to induce a vertical gradient in ionized mobile charge (e.g., H ⁺ ) in an ambient humid environment. The diffusion of the mobile charges leads to electric potential similar to that in a biological cell membrane. However, the power output of devices according to this strategy are only capable of producing brief bursts (less than 50 sec) of current (around 0.9 pA/cm ² , or a power density around 30 pW/cm ³ ) before the device voltage collapses. Re-establishing the voltage (to around 0.2 V or 20 V/ cm) through self- recharging, then requires around 100 s. Accordingly, the charging time greatly exceeds the time of power output. Additionally, slow decay in current generation is likely due to induced gradual modification of hydroxyl groups on graphene surface in the ambient environment.

Summary

A new device for sustainably and continuously producing electric power in the ambient environment is provided. Instead of relying on a liquid water source, the device can use moisture naturally present in the ambient environment in the form of atmospheric humidity. The device, therefore, can operate and continuously produce electric power where there is no liquid water source. The device is fabricated with conductive protein nanowires produced by the microorganism Geobacter sulfurreducens. The continuous power generation results from an depth-dependent humidity adsorption in the protein nanowire film. This creates a vertical moisture gradient in the protein nanowire film, as will be described herein. This moisture gradient results in a vertical charge gradient and the charge gradient, therefore, produces a steady electric field or DC voltage for powering electronics.

The power output of the disclosed invention is continuous and stable in the ambient environment. The output voltage can be maintained in devices of less than 1 mm ² (thickness of around 5 pm) and can yield an instant power density of around 13 kW/m ³ Even without optimization, this value exceeds a number of well- established energy-harvesting technologies. Furthermore, unlike solar panels that are inherently confined to a 2D-plane configuration, the technology described here can be stacked in 3D configurations (as moisture is 3D diffusive) to greatly increase the power output within a given square area.

The protein nanowire technology of the disclosed invention enables electric power generation from anywhere, at any time, in an ambient environment and thus is more versatile than existing technologies such as solar cells, wind turbines, and mechanical generators that are inherently intermittent and limited by environmental conditions.

Moreover, the thin film device of the disclosed invention can readily be “painted” on a diversity of surfaces (e.g., clothes, walls), and can therefore serve as the basis for“electronic fabrics” or be incorporated into a broad range of electronic devices, to provide instant electric power.

According to an aspect of the invention, an electric power generation system is provided. The electric power generation system includes an electric power generation device. The electric power generation device includes a thin film or biofilm of protein nanowires or a nanowire composite. The thin film or biofilm has an opposing first surface and second surface. The electric power generation device includes a first electrode electrically connected to the first surface of the thin film or biofilm, and a second electrode electrically connected to the second surface of the thin film or biofilm. The electric power generation system also includes an ambient environment including an atmospheric relative humidity of at least 20%.

At least one of the first surface and the second surface of the thin film or biofilm is at least partially exposed to the ambient environment, and a moisture gradient is created and maintained in the thin film or biofilm. In an embodiment, the protein nanowires are harvested from one or more of the microorganisms Geobacter sulfurreducens, Geobacter metallireducens, Syntrophus aciditrophicus, and Methanospirillum hungatei.

In another embodiment, the protein nanowires are genetically modified Aro- 5 nanowires.

In another embodiment, the protein nanowires are OmcS-pili nanowires.

In another embodiment, the protein nanowires are OmcS-OmcS pili nanowires.

In another embodiment, the protein nanowires are organic synthetic nanowires.

In another embodiment, at least two electric power generation devices are stacked in a three-dimensional configuration. At least one of the first surface and the second surface of the thin film or biofilm of each electric power generation devices are at least partially exposed to the atmospheric relative humidity in the ambient environment.

In another embodiment, the first electrode and the second electrode include one or more of gold, platinum, aluminum and carbon.

In another embodiment, the thin film has a thickness in the range of 0.5 pm - 500 pm.

In another embodiment, the atmospheric relative humidity is in the range of 30% - 90%.

According to another aspect of the invention, a method of continuously producing electric power using atmospheric relative humidity in an ambient environment is provided. The method includes providing an electric power generation device. The electric power generation device includes a thin film or biofilm of protein nanowires or a nanowire composite. The thin film or biofilm has an opposing first surface and second surface. The electric power generation device further includes a first electrode electrically connected to the first surface of the thin film or biofilm, and a second electrode electrically connected the second surface of the thin film or biofilm. The method then includes at least partially exposing at least one of the first surface and the second surface of the thin film or biofilm of the electric power generation device to the ambient environment, wherein the atmospheric relative humidity is at least 20%, and forming and maintaining a moisture gradient in the thin film or biofilm. The method then includes continuously generating power in the electric power generation device.

In an embodiment, the protein nanowires are harvested from one or more of the microorganisms Geobacter sulfurreducens, Geobacter metallireducens, Syntrophus aciditrophicus, and Methanospirillum hungatei.

In another embodiment, the protein nanowires are genetically modified Aro- 5 nanowires.

In another embodiment, the protein nanowires are OmcS-pili nanowires.

In another embodiment, the protein nanowires are OmcS-OmcS pili nanowires.

In another embodiment, the protein nanowires are organic synthetic nanowires.

In an embodiment, the method further includes providing at least two of the electric power generation devices and stacking the at least two electric power generation devices in a three-dimensional configuration. The method then includes at least partially exposing at least one of the first surface and the second surface of the thin film or biofilm of each of the electric power generation devices to the ambient environment, wherein the atmospheric relative humidity is at least 20%. The method then includes forming and maintaining a moisture gradient in the thin film or biofilm of each of the electric power generation devices, and continuously generating a power output from each of the electric power generation devices.

In another embodiment, the first electrode and the second electrode include one or more of gold, platinum, aluminum and carbon.

In another embodiment, the thin film has a thickness in the range of 0.5 pm - 500 pm.

In another embodiment, the atmospheric relative humidity is in the range of 30% - 90%.

In another embodiment, the power output is associated with the

atmospheric relative humidity. Brief Description of the Drawings

Fig. 1 is a schematic drawing of an electric power generation device in accordance with an aspect of the present invention, including TEM images of a nanowire network and the microorganism Geobacter sulfurreducens.

Figs. 2A-B are views of a pilus structure modeled by a molecular dynamics simulation.

Fig. 2C is a top view of the pilus structure modeled in Figs. 2A-B.

Fig. 3 is a graph showing a typical l-V curve from the electric power generation device of the present invention.

Fig. 4A is a graph showing the evolution of / and V ₀ the electric power generation device of the present invention in an ambient environment with a relative humidity of around 50%.

Fig. 4B is a graph showing the continuous recording of V ₀ from the electric power generation device of the present invention for 700 hours.

Fig. 4C is a graph showing the continuous recording of V ₀ from the electric power generation device of the present invention for 1500 hours.

Fig. 5A is a graph showing W _Hz0 % in protein nanowire films with respect to film thickness ( d ) at ambient RFI of around 50%.

Fig. 5B is a schematic of an analyzed vertical moisture gradient in the protein nanowire film.

Fig. 5C is a graph showing W _Hz0 % at different nanowire-film thicknesses (d). AW _{HZ 0} % = 2 x (27% - W _Hz0 %), is the estimated difference in moisture- adsorption ratios between the top and bottom interfaces. The blue curve shows V ₀ with respect to film thickness.

Fig. 5D is a graph showing the moisture adsorption/desorption dynamics in a nanowire film and in the same nanowire film after 5 days measured by using Quartz Crystal Microbalance (QCM) technique.

Fig. 6A is a schematic and graph showing residual V ₀ of around -50 mV from a symmetric nanowire device with both top and bottom surfaces sealed. Fig. 6B is a schematic and graph showing a nanowire device (1 *2 cm ² , around 7 pm thick) vertically aligned with moisture gradient above the water surface, with a pair of electrodes placed at either the top or bottom interface.

Fig. 6C is a schematic and graph showing V ₀ of around 0.8 V from a pair of top electrodes in a nanowire device with half of the top surface covered by a glass slide.

Fig. 7 A is a schematic and graph showing V ₀ with varied top electrode configurations in the electric power generation device.

Fig. 7B is a schematic and graph showing V ₀ from a pair of top electrodes, with half of the top surface covered by a glass slide. The lower curve shows a typical V ₀ from the pair of top electrodes without the glass cover.

Fig. 8A is a schematic of water vapor pressure (P _v ) lowering in a porous material and the existence of a vapor-pressure gradient close to air interface.

Fig. 8B is a schematic of the mechanism of charge donation to the nanowire film from ambient water clusters.

Fig. 8C is a schematic and graph showing that the continuous current output from a nanowire device in the ambient environment (RFI of around 45%) is disrupted when the top interface was covered with a parafilm (inset) and persisted (gray region) till the seal was removed, when the current began to restore its original value. A load resistor RL = 2 MW was used.

Fig. 9A is a graph showing V ₀ (upper curve) and / _sc (lower curve) with respect to device size at ambient RFI around 50%. The film thickness was kept at around 7 pm.

Fig. 9B is a graph showing V ₀ (upper curve) and / _sc (lower curve) with respect to film thickness ( d ) at ambient RFI around 50%. The film size was kept at around 1 mm ² .

Fig. 9C is a graph showing V ₀ (upper curve) and / _sc (lower curve) by connecting 5 nanowire devices in series and in parallel, respectively, compared to Vo (upper curve on bottom) and / _sc (lower curve on bottom) from an individual nanowire device. Fig. 9D is a picture showing the nanowire devices used to charge up capacitors to power a LED (left) or LCD panel (right).

Fig. 10A is a graph showing a 16 hour continuous recording of the open- circuit voltage ( ₀ ) from a nanowire device in the ambient environment.

Fig. 10B is a graph showing a 16 hour continuous recording of the short- circuit current (/ _sc ) from a nanowire device in the ambient environment (RH around 60%). The device sizes were 5x10 mm ² , the nanowire thickness was around 7 pm.

Fig. 11A is a schematic and graph showing the normalized weight of a protein-nanowire film, measured by quartz crystal microbalance before and after 4, 8, 24, and 36 hours of continuous current output.

Fig. 11 B is a graph showing Fourier transform infrared (FTIR) spectroscopy of the protein-nanowire film before and after an 18 hour continuous current output.

Fig. 12A is a graph showing open-circuit voltage ( ₀ ) maintained at ~0.55 V from a nanowire device (around 7 pm thick) after being exposed to the ambient environment for over 10 months.

Fig. 12B is a graph showing the current (/) output (with a load resistor of 2 MW) maintained at ~130 nA from a nanowire device (around 7 pm thick) after being exposed to the ambient environment for over 10 months.

Fig. 13 is a graph showing open-circuit voltage ( Vo) from a nanowire device exposed to different gaseous (e.g., air, nitrogen, and oxygen) environments, with the relative humidity (RH) kept constant around 53%.

Fig. 14 is a schematic and graph showing electric outputs from a protein- nanowire device at different load resistances (RL).

Fig. 15 is a graph showing V ₀ with respect to relative humidity. The device size was ~ 0.5x0.5 cm ² with film thickness around 7 pm.

Fig. 16A is a picture and schematic showing the setup for measuring moisture adsorption in nanowire films using a quartz crystal microbalance (QCM).

Fig. 16B is a graph showing a typical frequency response from the QCM.

Fig. 16C is a graph showing measured weight changes in nanowire films of different thicknesses. Fig. 17A is a schematic showing the existence of a moisture gradient where the average adsorption ratio ( I/1/H2O%) in a peel-off film (thickness d) is {W\ _op % + l/l/middie%)/2, where W\o _P % and W’mM\ _e % are the local adsorption ratios at the top and middle interfaces, respectively.

Fig. 17B is a schematic showing the existence of a moisture gradient for a symmetric diffusion from top and bottom interfaces, where W’mm\e% is the same as the bottom adsorption ratio ( l/l/bottom%) in a half-thick {d/2) film deposited on substrate (/. e. , bottom interface being sealed).

Fig. 17C is a graph showing measured adsorption ratios in peel-off nanowire films at different thicknesses, compared to those in on-substrate nanowire films.

Fig. 17D is a graph showing weight changes in nanowire films of different thicknesses, corresponding to data points of peel-off films in Fig. 17C, measured by QCM.

Fig. 18A is a graph showing the evolution of the open-circuit voltage {V ₀ ) in a nanowire device.

Fig. 18B is a graph showing a comparison between the V ₀ recovery process (upper curve) with a typical moisture re-adsorption process in the nanowire film (lower curve) measured by QCM.

Fig. 19A is a schematic and graph showing (Left panel) Molecular modeling of two pili nanowires interfacing with each other, with the arrows indicating the pores formed at the interface. (Right panel) Calculated maximal pore radius with respect to the relative position (Dc) of the two protein nanowires. The dashed line indicates the radius of a water molecule (around 0.14 nm).

Fig. 19B is a schematic and graph showing representative conformation of tightly packed OmcS-OmcS filaments (left) and calculated pore radius with respect to Dc (right).

Fig. 19C is a schematic and graph showing representative conformation of tightly packed OmcS-p/7/ filaments (left) and calculated pore radius with respect to Dc (right). Fig. 20 is a schematic showing a moisture gradient (represented by the cyan background) in the nanowire film.

Fig. 21 is a schematic showing current in a nanowire device.

Fig. 22A is a schematic and graph showing V ₀ (around 0 V) from thin film (around 10 pm thick) made from synthetic zinc-oxide (ZnO) microparticles.

Fig. 22B is a schematic and graph showing V ₀ (around 0 V) from thin film (around 10 pm thick) made from single-walled carbon nanotubes (SWCNTs).

Fig. 22C is a schematic and graph showing V ₀ (around 0 V) from thin film (around 10 pm thick) made from polyvinylpyrrolidone (PVP).

Fig. 22D is a schematic and graph showing V ₀ (around 0 V) from thin film (around 10 pm thick) made from potassium chloride (KCI) by evaporating KCI solution.

Fig. 23A is a graph showing open-circuit voltage measured from a thin film made from genetically modified nanowire (Aro-5) in the ambient environment (RFI around 50%).

Fig. 23B is a graph showing short-circuit current measured from a thin film made from genetically modified nanowire (Aro-5) in the ambient environment (RFI around 50%).

Fig. 24A is a graph showing electric output (open-circuit voltage) in nanowire film prepared from close-to-neural solution (pFH around 8).

Fig. 24B is a graph showing electric output (short-circuit current) in nanowire film prepared from close-to-neural solution (pFH around 8).

Fig. 25A is a schematic and graph showing open-circuit voltage ( V ₀ around 0 V) from control devices made from SWCNTs added with HCI.

Fig. 25B is a schematic and graph showing open-circuit voltage (V ₀ around 0 V) from control devices made from hygroscopic PVP added with HCI.

Fig. 26 is a schematic and graph showing reversible current output from a nanowire device with respect to the change in relative humidity (RFI).

Fig. 27 A is a schematic showing (Left panel) a device structure used for voltage/current scaling study and (Right panel) a top-view current distribution in the nanowire device simulated by using the finite element method (COMSOL 4.3). Fig. 27B is a graph showing changes in resistance in the nanowire devices with respect to changes in device size from (upper curve) experiment (/. e. , Vo/lsc) and (lower curve) simulation, respectively.

Fig. 28 is a graph showing an estimated upper limit of power output for the electric power generation device according to the present invention.

Fig. 29A is a schematic of a measurement setup of the electric power generation device according to the present invention.

Fig. 29B is a graph of the measured V ₀ and / _sc from the device in the ambient environment (RFI around 55%), showing similar value to that in open air.

Fig. 30 is a schematic and graph showing voltage output from connected nanowire devices in series.

Fig. 31 is a schematic and graph showing charging to capacitor using nanowire devices.

Fig. 32A is a schematic showing a Ge-Si core-shell nanowire transistor. The S, D and G denote source, drain and gate electrodes, respectively. The right panel shows a dark-field optical image of the fabricated nanowire transistor. Scale bar, 1 pm.

Fig. 32B is a graph showing a typical transfer curve from the transistor powered by external voltage \/ds = 1 V.

Fig. 32C is a schematic showing the use of a protein-nanowire device to power the Ge-Si nanowire transistor.

Fig. 32D is a graph showing source-drain current (/ds) at different gate voltages ( Vg _S ) measured from the transistor.

Fig. 33A is a schematic showing a fabrication process of the electric power generation device according to the present invention.

Fig. 33B is a scanning electron microscopy (SEM) image of a typical nanowire thin film. Scale bar, 10 pm.

Fig. 33C is a transmission electron microscopy (TEM) image of the nanowire film at relatively high density.

Fig. 33D is a TEM image of the nanowire film of Fig. 33C at low density. Scale bars, 100 nm. Fig. 33E is a TEM image of the nanowire film of Fig. 33C at medium density. Scale bars, 100 nm.

Fig. 33F is an image of an as-fabricated nanowire device array on a glass slide with different bottom-electrode sizes (e.g., 1 , 4, 9, 16, 25 mm ² ).

Fig. 33G is an image of typical nanowire devices using (top panel) braided gold-plated wire or (bottom panel) gold-coated PET stripe as the top electrodes.

Fig. 34A is a schematic and graph showing an open-circuit voltage ( Vo) recorded from a nanowire device using a pair of top and bottom carbon electrodes in the ambient environment (RFI around 50%).

Fig. 34B is a schematic and graph showing an open-circuit voltage ( Vo) recorded from a nanowire device using a pair of commercial glassy carbon electrodes in the ambient environment (RFI around 40%).

Detailed Description

The present disclosure is directed to a method of generating continuous electric power using an electric power generator having a thin film of protein nanowires, for example, protein nanowires harvested from the microorganism Geobacter sulfurreducens. The electric power generator of the present disclosure generates continuous electric power in the ambient environment, producing sustained voltage of, for example, around 0.5 V across a 7 pm film thickness with a current density of around 17 pA/cm ² . The driving force behind this phenomenon is the self-maintained moisture gradient that forms within the film when exposed to the atmospheric humidity naturally present in ambient environments. Connecting multiple devices linearly can scale up voltage and current to power a wide variety of electronics, such as for example wearable personal electronics, portable energy sources, and mobile devices. The electric power generator disclosed herein can produce continuous electric power from ambient atmospheric moisture with 100- fold improvement in power density over previously known devices.

Fig. 1 depicts an exemplary structure of an electric power generator device 10 (bottom image) according to an aspect of the present disclosure. As depicted, a thin film of protein nanowires 12 is deposited on a first electrode 14. The thin film of protein nanowires 12 may be, for example, around 7 pm thick. The thin film, however, may be anywhere in the range of, for example, 0.5 pm - 20 pm, 1.0 pm - 15 pm, 2.0 pm - 10 pm, 3.0 pm - 8.0 pm, 4.0 pm - 7.0 pm, or 5.0 pm - 6.0 pm. The first electrode 14 may be, for example, made of gold (Au), platinum (Pt), aluminum (Al), carbon (C) or other suitable materials. The first electrode 14 may have an area of around 25 mm ² . The first electrode 14 may, however, have any area that is the same size or smaller than the area of the protein nanowire film.

The first electrode 14 may be patterned on a glass substrate 18. A second electrode 16 is disposed on top of the thin film of protein nanowires 12. The second electrode 16 may have an area of around 1 mm ² or may have any area that is smaller than the area of the protein nanowire film to allow exposure of the protein nanowire film to the ambient atmosphere. The second electrode 16 may be, for example, made of Au, Pt, Al, or other suitable materials, similar to the first electrode 14. The second electrode 16 may be in a mesh form, or may otherwise be porous. The first and second electrodes 14, 16 are positioned on opposing surfaces of the thin film of protein nanowires, so as to measure an electric field or DC voltage through the thin film. At least one surface of the thin film is at least partially exposed to the ambient environment so that ambient atmospheric humidity can reach the thin film.

The protein nanowires 12 may be, for example, pili sheared from the microorganism Geobacter sulfurreducens (GS). In an embodiment, the pili are electrically conductive. Examples of other protein nanowires include the protein nanowires produced by the bacterium Geobacter metallireducens (GM). These wires have the same diameter (3 nm) as the GS wires, but are 5,000-fold more conductive. The protein nanowires produced by bacterium Syntrophus

aciditrophicus (SA) may also be used. These wires are only slightly thicker (4 nm) than the GS wires and have similar conductivity. The protein wires produced by the archaeon Methanospirillum hungatei (MH) may also be used and are of somewhat larger diameter (10 nm) and more conductive than the GS wires. In addition, the gene for the pilin monomer that GS assembles into protein nanowires can be modified to yield“synthetic protein nanowires” with higher conductivities as described in U.S. Patent Publication No. 2018/0371029A1 , which is incorporated herein by reference. The protein nanowires 12 may also be produced from expression of the pillin genes of various bacteria and archaea in an appropriate host organism. For example, the protein nanowires may be variants of various pillin genes that exist in nature.

Fig. 1 also depicts transmission electron microscopy (TEM) images of the microorganism GS (top left image) and the purified nanowire network produced by GS (top right image), with the depicted scale bar representing 100nm. As depicted, the protein nanowires 12 have an average diameter of around 3 nm and an average length of around 1 -3 pm and form a mesh network in the film.

In one embodiment, the protein nanowire film 12 is a conductive microbial protein nanowire (c-MPN) film. A c-MPN is a microbial pilus that assembles from a single peptide subunit known was a pilin. Each pilin’s N-terminal (N -t) bonds to a neighboring one through helical salt bridge with around 10.5 A raise to form the pilus core, depicted in Figs. 2A-B. The C-terminal (C -t), however, is a flexible end slightly bent way from the axis of the pilus core and considered as electron- exchange site for GS’ extracellular reduction of iron oxides. Together, the pilus features an average diameter of around 35 A (the core) with a helical bulge of around 47 A (the C -t) in solution (Fig. 2B). Under dehydration, the C -t contracts and yields a reduced helical bulge (e.g., around 40 A). Such conformational change effectively produces swelling and deswelling in individual pilus at hydrated and dehydrated states, respectively (Fig. 2C). For the close packing between c- MPNs revealed by TEM, the deswelling and swelling effectively turn ON and OFF the molecular channels (i.e., inter-pilus spacing) of water vapor passing through the c-MPN film. This means that in an initially dehydrated c-MPN film, atmospheric moisture goes through the film and reaches the bottom interface to form residual moisture. Flowever, as the top surface adsorbs moisture at a faster rate (due to proximity to atmospheric moisture) and reaches a completely hydrated/swelled state, all the molecular channels for water passage are closed in the top surface layer and the c-MPN layer beneath no longer has a moisture supply. This is how the moisture gradient is created and maintained in the thin film. As such, a dehydrated c-MPN film, which does not produce voltage output initially, gradually builds up a voltage when placed in the ambient environment. Moreover, a c-MPN film in the ambient environment is water vapor tight, whereas a dehydrated film is not. Meanwhile, the high-density (around 1 nrrr ¹ ) carboxylic groups innate to c-MPN tend to be protonated in the hydrated state. The moisture gradient creates a gradient in protonation or a concentration gradient of the mobile protons that is similar to the membrane potential in biological systems. The downstream sides are the high potential (+) side. The charge diffusion also determines that a potential/voltage difference is proportional to an ion- concentration difference. Accordingly, a moisture difference (assume ionization is proportional to adsorbed moisture) determines the output voltage.

In other embodiments, the protein nanowires may involve different species, such as genetically modified Aro-5 nanowires, OmcS-OmcS nanowires, and/or OmcS-pili nanowires. Additionally, synthetic protein nanowires may be used, as described above. In these embodiments, the protein nanowires are known to have non-uniform diameters with periodic surface structures along the axis. As a result, nanometer-scale pores or nanopores form at nanowire-nanowire interface in the protein nanowire film. An average nanopore size may be, for example, in the range of 0.1 nm - 10 nm in the largest dimension. Even at the most compact stacking configuration in different wires, there still exist nanopores that allow for water molecule passage. The nanowires are randomly distributed, indicating a wide distribution of nanopores.

In any embodiment, the existence of a high density of these nanopores in the film helps to account for the existence and self-maintenance of a moisture gradient within the thin film when the thin film is exposed to ambient atmospheric humidity. Specifically, vapor pressure lowering is generally observed in porous medium due to the contribution of a capillary pressure, and this effect is stronger for smaller pore size. In fact, for water vapor, substantial effect can be observed at a nanometer-scale pore size, which the protein nanowire film of the present disclosure has. At steady state, a vapor-pressure gradient exists at the air-material interface. For a thin nanowire film (e.g., less than 7 pm thick), the entire thickness is within this interfacial gradient, whereas thicker nanowire films extend over the finite gradient region. Furthermore, water adsorption at a solid surface is a dynamic equilibrium involving constant adsorption-desorption exchange at the interface. In a general recombination dynamic, the adsorption is proportional to molecular concentration or the vapor pressure. As a result, the induced vapor pressure gradient in the nanowire film leads to a moisture gradient. Saturation in the vapor- pressure difference for thicker film leads to a saturation in moisture-adsorption difference (AW _H20 %).

The moisture gradient accounts for the voltage generation in the nanowire films of the present disclosure. The surface functional groups (e.g., carboxylic group) innate to the nanowires are a source of exchangeable protons. The moisture gradient creates an ionization gradient in the carboxylic groups or a concentration gradient in mobile protons (against an immobile -COO anionic background). The proton gradient leads to its diffusion, further facilitated by a hole- like conduction in the nanowire. This charge diffusion induces a counterbalancing electrical field or potential analogous to the resting membrane potential in biological systems. The lower-moisture side always has higher (+) potential. In particular, the built-up voltage is proportional to the difference in proton

concentration, which is considered closely related to AW _Hz0 %. This is consistent with the fact that AW _Hz0 % is closely correlated with output voltage. A high density of nanopores helps to form the moisture gradient, and a high density of surface functional groups subsequently leads to a potential gradient by charge diffusion in the film. In contrast, other devices made from other porous thin films, which feature either larger pore sizes or nanoscale pores without functional groups, do not yield electric output. The maintained moisture gradient, which is fundamentally different from all previous systems, results in the continuous voltage output of the electric power generator device 10 disclosed herein.

According to an aspect of the present disclosure, therefore, a method of producing continuous electric power using atmospheric relative humidity in an ambient environment is provided. The method includes providing an electric power generation device. The electric power generation device includes a thin film, or biofilm, of protein nanowires or a nanowire composite, as previously described.

The thin film has an opposing first surface and second surface. The thin film may be, for example, around 7 pm thick. The thin film, however, may be anywhere in the range of several pm to hundreds of pm. For example, the thin film may be anywhere in the range of 0.5 pm - 500 pm, 1.0 pm - 250 pm, 2.0 pm - 100 pm,

3.0 pm - 50 pm, 4.0 pm - 25 pm, 4.0 pm - 10 pm, 4.0 pm - 7.0 pm, or 5.0 pm - 6.0 pm.

A first electrode is electrically connected to the first surface of the thin film and a second electrode is electrically connected to the second surface of the thin film. As the first and second electrodes are electrically connected to opposing surfaces of the thin film of protein nanowires, the first and second electrodes measure an electric field or DC voltage through the thin film. The first electrode 14 may be, for example, made of gold (Au), platinum (Pt), aluminum (Al), carbon (C) or other suitable materials. The first electrode 14 may have an area of around 25 mm ² . The first electrode 14 may, however, have any area that is the same size or smaller than the area of the protein nanowire film. The first electrode may be patterned on a glass substrate. The second electrode 16 may have an area of around 1 mm ² or may have any area that is smaller than the area of the protein nanowire film to allow exposure of the protein nanowire film to the ambient atmosphere. The second electrode 16 may be, for example, made of Au, Pt, Al, or other suitable materials, similar to the first electrode 14. The second electrode 16 may be in a mesh form, or may otherwise be porous.

The method then includes exposing at least one of the first surface and the second surface of the thin film of the electric power generation device to the ambient environment. In this way, moisture from the ambient environment, in which the atmospheric relative humidity is at least 20%, can reach the thin film.

The atmospheric relative humidity, however, may be anywhere in the range of 20% - 100%, 30% - 90%, 40% - 80%, and 50% - 70%. When moisture reaches the thin film, the method then includes forming and maintaining a moisture gradient in the thin film and, therefore, continuously generating power in the electric power generation device, according to the mechanisms and concepts described herein. With reference to Fig. 3, an exemplary current voltage ( l-V) output from the electric power generator device 10 (depicted in Fig. 1 ) is depicted when operated under ambient lighting (upper curve) versus in the dark (lower curve), at a ambient relative humidity (RFI) around 50%. As depicted, the l-V between the first electrode 14 and the second electrode 16 shows approximately linear behavior. As depicted, the l-V curve does not pass the origin, showing an open-circuit voltage (Vo) of around 0.5 V and short-circuit current (/ _sc ) of around -250 nA. This effect is robust and highly reproducible, with a uniform Vo (0.53 ± 0.03 V, N= 16) from different devices of the same film thickness. Moreover, the non-zero output is independent of light illumination and is maintained in a completely dark

environment (lower curve), indicating the lack of photovoltaic effect. Both V ₀ and / _sc are stable and last greater than 12 hours, indicating that the power output is not a transient phenomenon caused by a charge/capacitive effect during the

measurement.

The electric power generator device 10 of the present disclosure is different from a typical chemical cell as no living microorganism or chemical is fed to the system. Instead, the protein nanowires 12 are environmentally stable and do not decompose even in harsh (e.g., pH 2-10) solution. Accordingly, it is understood that the continuous voltage is not due to chemical decomposition of the protein nanowires over time. Additionally, inert material in (Au) electrodes reduces the possibility of a redox reaction from the electrodes contributing to output voltage. Moreover, because a similar electric output results from inert carbon electrodes, it is understood that the observed voltage is not due to the electrode material.

Furthermore, removal of oxygen or nitrogen from the gas phase had no impact on the generation of the voltage whatsoever. The generation of voltage in the electric power generator device 10 is therefore understood to be affected by the relative humidity available from atmospheric moisture.

Continuous V ₀ recording, depicted in Figs. 4A-C, shows that the electric power generator device 10 of the present disclosure maintains a stable DC baseline over a significant period of time. With reference to Fig. 4A, the evolution of / and from the electric power generator device 10 in an ambient environment having a relative humidity around 50% is depicted. Generally, Fig. 4A depicts how the device 10 maintains a stable DC baseline of around 0.35-0.5 V for over 20 hours. After 20 hours of current production, the voltage declines, but is restored within 5 hours. After an additional 20 hours, the voltage is again slightly reduced, but can be repeatedly self-recharged.

Specifically, Fig. 4A depicts that the device 10 initially has a V ₀ of around 0.52 V for the first 5 hours of operation. Connecting the device 10 to a load resistor {RL = 2 MW) yields a continuous and gradually stabilized / of around 110 nA for 20 additional hours. When RL is disconnected and the V ₀ is recorded (indicated by the arrow at t = 25 hours), V ₀ gradually increases to the initial value of 0.5 V for the next 5 hours (25 < t < 30h), showing a self-recharging process. Re-connecting to RL yields a repeated continuous powering to the RL (/ of around 115 nA; 30 < t <

50 h). Disconnecting the RL yields a 2 ^nd self-recharging process (50 < t < 55 hours), bringing V ₀ back to 0.5 V. The inset in Fig. 4A depicts the circuit diagram, in which connections to terminal and‘2’ correspond to / and Vo measurements, respectively.

Fig. 4B generally depicts how the device 10 maintains a stable DC baseline of around 0.4-0.5V (upper curve) for over 700 hours (1 month). Furthermore, Fig. 4C generally depicts how the device 10 maintains a stable DC voltage of around 0.4-0.6 V for over 1 ,500 hours (2 months). Fluctuations in voltage are associated with changes in the ambient relative humidity (RH; lower curves). Both the field amplitude (around 700 V/ cm) and sustainability in the voltage are a more than 10- fold improvement over the best results from previous ambient generators (e.g., around 40 V/ cm for 120 hours). In a controlled humidity environment, around 40- 50% RFI yielded the highest voltage, but substantial voltages were still generated at RFI as low as 20% (e.g., comparable to desert environment) as well as at 100 % humidity). This output trend contrasts with carbon-based ambient electric generators which show a unidirectional increase in output voltage with increasing RH.

With reference to Fig. 5A, the moisture adsorption ratio (l Vwater%), defined as the weight of adsorbed moisture over the total weight of protein nanowire film and measured by a quartz crystal microbalance, is inversely proportional to film thickness ( d ) in the device 10 at an ambient RH of about 50%. As depicted, l l/water% reaches around 27% for thin films (i.e. , less than 1 pm thick) and retains around 15% for thick films (i.e., greater than 8 pm thick). This film thickness- dependent adsorption is supported by Fourier-transform infrared spectroscopy.

This trend can be largely accounted for by a vertical moisture gradient in the protein nanowire film, depicted schematically in Fig. 5B. Fig. 5C depicts that the AW _Hz0 % = 2 x (27% - W _Hz0 %) is the estimated difference in moisture-adsorption ratios between the top and bottom interfaces of the thin film. The upper curve shows Vo with respect to film thickness. Fig. 5C indicates around a 27%

adsorption ratio at surface area (e.g., less than 1 pm depth) and close to 3% at the bottom (e.g., greater than 8 pm depth) to yield an average ratio of around 15% in thick films. Modeling this apparent difference in moisture adsorption (AW _Hz0 %) between the top (exposed) and bottom (sealed) interfaces demonstrates a clear correspondence between increasing AW _Hz0 % and increasing V ₀ up to a plateau of around 0.55 V for thick films with d around 10 pm. Moisture contents, and thus presumably the proposed moisture gradients, remain stable over time, as depicted in Fig. 5D, which is consistent with the long-term stability of V ₀ , depicted in Figs. 4A-C. As depicted in Fig. 5D, the moisture adsorption/desorption dynamics in the nanowire film and in the same nanowire film after 5 days measured by using a QCM technique did not change, reflected by the very close amplitudes in the change of resonance frequency (Af). The moisture gradient built up from a non- gradient ambient environment is fundamentally different from all previous moisture- based technologies which lack this capability.

Further evidence for the importance of the adsorption-difference induced moisture gradient to generate voltage was the observation that a voltage was not generated when the top film was also completely covered with a gold electrode, as depicted in Fig. 6A. Fig. 6A depicts a residual V ₀ of around -50 mV from a symmetric nanowire device with both top and bottom surfaces sealed. Additionally, horizontally adjacent top or bottom pairs of electrodes produce near-zero voltages, as no horizontal moisture gradient is produced in the protein nanowire film. However, if the film is rotated so that the horizontally adjacent electrodes are vertically positioned over water to produce a moisture gradient between the two electrodes, then a voltage is produced, as depicted in Fig. 6B. A pair of electrodes placed underneath the film produced a considerably smaller voltage, consistent with the expected lower moisture adsorption at depth. Alternatively, creating an adsorption difference and hence a moisture gradient between two top electrodes by covering a portion of the film with a glass slide also generated a stable voltage, such as around 0.8 V, as depicted in Fig.6C.

Furthermore, when a pair of vertical electrodes that initially produces a constant V ₀ of around 0.5 V in ambient environment (Fig. 7 A, where t is less than 3h) is modified so that the top electrode is replaced with a film electrode on a glass slide that prevents exposure of the top protein nanowire film surface to the ambient environment, the voltage output drops to close to 0 V (Fig. 7 A, where t is greater than 3 and less than 6 hours). Switching back to the point electrode returns V ₀ back to around 0.5 V (Fig. 7 A, where t is greater than 6 hours). On the other hand, for a pair of horizontal electrodes that initially produces close-to-zero V ₀ (Fig. 7B, lower curve), covering half of the top film surface yields substantially increased V ₀ around 0.8 V (Fig. 7B, upper curve). These results indicate that the built-up moisture gradient in the protein nanowire film is a dynamic equilibrium involving constant moisture exchange with ambient environment. Such indication is consistent with a fast moisture adsorption/desorption rate in the protein nanowire film. The dynamic moisture exchange is also the basis of a continuous energy input for power output. This dynamic moisture gradient built up out of a non- gradient ambient environment is completely different from previous systems which are incapable of producing self-supported moisture gradient, and hence forms a fundamentally different basis for continuous power generation.

With reference to Figs. 8A-C, a mechanism for energy harvesting in the nanowire film is described. Fig. 8A depicts a schematic of vapor pressure ( P _v ) lowering in a porous material and the existence of a vapor-pressure gradient close to the air interface. Air water clusters naturally contain ionized species or may be ionized when adsorbed on the nanowire surface. The ionized clusters (e.g., H(H2q)h7HO(H2q)h ) donate charge ( e.g ., H7e ) to the nanowire, as depicted in Fig. 8B, which supplies the close-loop current flow driven by the voltage resulted from moisture gradient. Dynamic adsorption-desorption exchange of water clusters at the interface provides the continuous input. The ambient environment provides a large reservoir for continuous exchanges required for sustained electric output.

Fig. 8C depicts how the continuous current output from a nanowire device in the ambient environment (RFI of about 50%) was disrupted when the top interface was covered with a parafilm (see insert). The current disruption persisted until the seal was removed, when the current began to restore its original value).

The device shows a wide operation window with respect to relative humidity in the ambient environment, which indicates that it can still function even in desert areas having low relative humidity. The device can produce a power output, for example, anywhere in the range of 20% - 100%, 30% - 90%, 40% - 80%, and 50% - 70% relative humidity. An optimal V ₀ , however, is found to be at around 40-50% relative humidity, which is close to typical ambient relative humidity. This output trend is different from previous carbon systems, where a unidirectional increase in power output with increasing relative humidity was observed. The results demonstrate that although moisture adsorption is likely to result in the current output, the output is not directly correlated with a total moisture adsorption.

The device 10 according to the disclosed invention may be reduced in size and multiple devices may be connected in series or in parallel to linearly increase the output voltage or current. For example, a V ₀ around 0.5 V may be maintained even with a device size reduced to around 1 mm ² , whereas short-circuit current (/sc) may be gradually decreased to around 170 nA, as depicted in Fig. 9A. The reduction in / _sc is a direct result from the non-linear increase in film resistance between a pair of point-to-area asymmetric electrodes. With reference to Fig. 9B, the areal power density increases with the increase of film thickness and saturates at around 22 pW/cm ² at a film thickness of around 14 pm, which is consistent with the trend of voltage output previously described. This power output is estimated to be around 16% of the theoretical upper limit, described later herein with reference to Fig. 28. The converted volumetric power density of around 16 mW/cm ³ is more than two orders of magnitude larger than those from previous carbon-based systems.

As ambient humidity is 3D diffusive, stacking thin-film devices in the vertical direction with a 1 : 1 film-airgap ratio can lead to practical volumetric power density greater than 5 kW/m ³ , potentially outperforming solar cells which are intrinsically surface confined. Multiple devices could be connected in series or in parallel to linearly increase the output voltage or current, like a battery (see Fig. 9C). For example, an output voltage of 10 V may be achieved by serially connecting 17 devices. As the device is thin (e.g., less than 7 pm thick), a vertical stacking can yield practical high-power and area-efficient output. Connected devices can be used to charge up a capacitor to power up a LED or a LCD, for example, as depicted in Fig. 9D. The device may also be used to power a logic device made from semiconductor nanowire, in which the generator provides the source-drain power to a nanowire transistor. This nanowire powered transistor shows typical p- type transistor behaviors. Such logic control and signal amplification without an external power supply can result in low-cost, self-supported, and environment- driven sensing and computation.

Experimental:

Continuous voltage and current from nanowire devices. With reference to Fig. 10A, a 16 hour continuous recording of the open-circuit voltage (V ₀ ) from a nanowire device in the ambient environment is depicted. With reference to Fig.

10B, a 16 hour continuous recording of the short-circuit current (/ _sc ) from a nanowire device in the ambient environment (RH around 60%) is depicted. In both instances, the device size is 5x10 mm ² and the nanowire thickness is around 7 pm.

Characterizations of protein-nanowire properties during electric outputs. With reference to Fig. 11 A, a normalized weight of a protein-nanowire film, measured by quartz crystal microbalance before and after 4, 8, 24, and 36 hours of continuous current output, is depicted. The weight change/fluctuation was negligible (e.g., less than 0.5%) and within the measurement error. (Inset) The protein-nanowire film (around 7 pm thick, size ~0.2 cm ² ) was directly deposited on the quartz resonator with the resonator (Au) electrode also serving as the bottom electrode for the nanowire film; an Au wire served as the top electrode. The relative humidity was kept at 45% throughout the measurements. With reference to Fig. 11 B, Fourier transform infrared (FTIR) spectroscopy of the protein-nanowire film before and after an 18 hour continuous current output. The lack of change in adsorption peaks (e.g., frequency shift, intensity) is a strong indication of the lack of redox process.

Electric outputs from a nanowire device (around 7 pm thick) after being exposed to the ambient environment for over 10 months. With reference to Fig. 12A, the open-circuit voltage (V ₀ ) maintained at around 0.55 V. With reference to Fig. 12B, the current (/) output (with a load resistor of 2 MW) maintained at around 130 nA. The measurements were performed at a relative humidity of around 50%. The results were close to values obtained from relatively fresh samples.

Performance dependence on gaseous environments. With reference to Fig. 13, open-circuit voltage (V ₀ ) from the same nanowire device exposed to different gaseous (e.g., air, nitrogen, and oxygen) environments is depicted, with the RFI kept constant at around 53%. The curves show that V ₀ was largely independent of the gaseous environment with RFI kept constant.

Electric outputs from a protein-nanowire device at different load resistances ( RL ). With reference to Fig. 14, the testing was performed in the ambient environment with a RFI of around 45%.

Vo with respect to relative humidity. With reference to Fig. 15, the device size was around 0.5x0.5 cm ² with film thickness of around 7 pm.

Measurement of moisture adsorption in nanowire films. With reference to Fig. 16A, a setup for measuring moisture adsorption in nanowire films using a quartz crystal microbalance (QCM) is depicted. The nanowire thin film was coated on the quartz crystal resonator (right top) using a PDMS mold. The mass sensitivity of the QCM originates from the dependence of the oscillation frequency on the total mass of the metal-coated crystal, including any adlayers of deposited material. The mass change can be determined by Am = -Af A where fo, A,

2/0

p, m are resonant frequency of crystal's fundamental mode, area of the gold disk on the crystal, crystal's density (2.684 g em ^-3 ) and shear modulus of quartz

(2.947x10 ¹¹ g cm ¹ s ² ), respectively. Using this, the mass/weight of the coated nanowire film ( l/l/nw) in ambient environment (with adsorbed moisture) was first determined. Then the resonator was placed in a sealed container with dry air flowing in to reduce the RH to around 0% inside to drive away adsorbed moisture in the nanowire film. During the process, the mass change (D l/l/nw), which corresponds to the amount of moisture loss in the pili film, was continuously monitored by the QCM. The moisture adsorption ratio W _Hz0 % in the pili film can be determined as: W _H20 % = A l/l/nw/l/l/nwx 1 00%.

With reference to Fig. 16B, a typical frequency response from the QCM is depicted. The lower, straighter line is the response from the bare quartz crystal resonator before and during dry-air flowing, showing no signal change or mass change. The upper curved line shows the frequency response from a nanowire- coated crystal resonator, with the first and second arrows indicating the start and stop of dry-air flow, respectively. The moisture re-adsorption time (e.g., around 300 s, gray region) is consistent with a voltage building-up time (e.g., around 300 s).

Fig. 16C depicts measured weight changes in nanowire films of different

thicknesses (corresponding to moisture content).

Moisture adsorption in peel-off nanowire films. With reference to Figs. 17A-D, the existence of moisture gradient can be further verified. If a moisture gradient existed (/. e. , the local adsorption would be dependent on its depth from the interface), then exposing both interfaces would yield increased moisture adsorption. Specifically, with reference to Fig. 17A, the average adsorption ratio {W’H2O%) in a peel-off film (thickness d) is {W\ _op % + l/l/middie%)/2, where W\ _op % and l/l/middie% are the local adsorption ratios at the top and middle interfaces, respectively. With reference to Fig. 17B, for a symmetric diffusion from top and bottom interfaces, l/l/Widie% is the same as the bottom adsorption ratio ( l/l/bottom%) in a half-thick {d/2) film deposited on substrate (/.e., bottom interface being sealed). This indicates that (before saturation) the average adsorption ratio in a peel-off film is similar to that in a half-thick on-substrate film, or its thickness dependence (slope) is half of that in on-substrate films. With reference to Fig. 17C, measured adsorption ratios in peel-off nanowire films at different thicknesses (upper dots), compared to those in on-substrate nanowire films (lower dots) are depicted. The linear fitting (dashed lines) yielded a slope of -0.95% pm ¹ in peel-off films, which was close to half the value (-1.77% pm ^-1 ) in on-substrate films. With reference to Fig. 17D, weight changes in nanowire films of different thicknesses, corresponding to data points of peel-off films in Fig. 17C, measured by QCM are depicted.

Moisture adsorption-dependent voltage. With reference to Fig. 18A, evolution of the open-circuit voltage (V ₀ ) in a nanowire device is depicted. The downward facing arrow indicates the stage when the nanowire device was placed on a hot plate (around 80 °C) to drive out the initially adsorbed moisture. The upward facing arrow indicates the stage when the device was removed from the hot plate and placed in ambient environment, showing a recovery in Vo. With reference to Fig. 18B, comparison between the V ₀ recovery process (upper curve, corresponding to gray region in Fig. 18A) with a typical moisture re-adsorption process in the nanowire film (lower curve) measured by QCM. The two curves show similar recovery rates.

Molecular modeling of nanowire-nanowire interfaces. The simulation details are described in the Materials and Methods below. With reference to Figs. 19A-C, the nanowire-nanowire interface in the simulation involved two nanowire filaments in parallel configurations. The axis of both filaments is along the x direction. One filament was designated as the reference and the other filament was shifted in both x- and y-directions with respect to the reference filament and rotated along the filament axis to identify the most stable packing configurations. With reference to Fig. 19A (left panel), molecular modeling of two pili nanowires interfacing with each other is depicted, with the arrows indicating the pores formed at the interface. The right panel depicts calculated maximal pore radius with respect to the relative position (Dc) of the two protein nanowires. The dashed line indicates the radius of a water molecule (around 0.14 nm). With reference to Fig. 19B, representative conformation of tightly packed OmcS-OmcS filaments (left) and calculated pore radius with respect to Dc (right) are depicted. With reference to Fig. 19C, representative conformation of tightly packed OmcS-p/7/ filaments (left) and calculated pore radius with respect to Dc (right) are depicted.

Analysis of moisture-dependent output voltage in nanowire device. With reference to Fig. 20, a schematic shows the moisture gradient (represented by the cyan background) in the nanowire film based on experimental observation. The nanowire contains a high-density carboxylic groups (-COOFI). At higher moisture adsorption, a larger percentage of the carboxylic groups will be ionized (forming FT and -COO ions). Therefore, an ionization gradient will form following the moisture gradient. Since the proton or FT is mobile (against an immobile - COO anionic background), it will lead to FT diffusion from top to bottom (blue arrow). The diffusion current density can be expressed as ] _Diff = -qD , where

q, D, C represent the carrier charge, diffusion coefficient, and concentration of FT ions in the nanowire film. The diffusion results in a (positive) charge accumulation at the bottom surface and a negative anionic background at the top, creating an electric field (E) that will counterbalance the charge diffusion (black arrow). The drift current density caused by this field can be expressed as J _Dri f _t = a ^nw E, where a ^nw represents the electric conductivity in the nanowire film. The net current in the nanowire film will be At equilibrium

(open-circuit) state, net current J = 0, which leads to

As the nanowire film is thin (e.g., several pm), the concentration gradient can be

AC

approximated as— where Ac, and h represent the difference in FT concentration

between the top and bottom interfaces and thickness in nanowire film, respectively. Note that E = , where Vo is the open-circuit voltage. Eq. (1 ) yields

Although the actual ionization or FT concentration is subjected to molecular dynamics that requires further investigation, a reasonable assumption is that the ionization can be approximately proportional to the availability of water molecules or the moisture-adsorption ratio (W _Hz0 %) in the nanowire film. Therefore, we would expect V ₀ or that the open-circuit voltage (V ₀ ) would be proportional to the moisture difference W _Hz0 % between the top and bottom interfaces.

Current in nanowire device. With reference to Fig. 21 , following discussion from Fig. 20 above, at steady state, the nanowire film has a balance or cancellation between the drift current ( /drift) and diffusion current {l ): eq. (3),

where A represents the size of the device. If the nanowire device is connected to an external circuit, an additional path for the drift current is created. Therefore:

represent the drift- current components passing through the nanowire film and external circuit, respectively. In other words, an external circuit takes out portion of the initial internal drift current in an open-circuit nanowire device. Re-writing Eq. (4) yields

where R ^nw , R, V represent the nanowire-film resistance, external load resistance, and final output voltage, respectively. For open circuit, R- and by using s ^rai =

RpUi-h , Eq. (5) goes back to Eq. (2) that describes open-circuit voltage V _0.

Consequently, Eq. (5) yields

where V ₀ , /drift represent the output voltage and internal drift current (equivalent to short-circuit current / _sc ) in an open-circuit nanowire device, respectively. I^ _rift corresponds to the measured current (/) through the load resistor R. Eqs. (6), (7) indicate that when the nanowire device is connected to a load resistor R, both the output voltage V and measured current / will gradually drop from V ₀ and / _sc to V ₀ and (—— 7 _SC ; disconnecting the load resistor R will increase the voltage back to V ₀ (re-charging process). These analyses are consistent with the voltage and current trends in the self-recharging process observed experimentally. Note that above analyses are based on the assumption that the H ⁺ concentration difference AC across the nanowire film thickness is kept constant.

Open-circuit voltage ( V ₀ ) measured from control devices in the ambient environment (RH around 50%). With reference to Fig. 22A, Vo (around 0 V) from thin film (around 10 pm thick) made from synthetic zinc-oxide (ZnO) microparticles is depicted. The film featured a high density of pores larger than molecular scale due to a spiked morphology in the microparticles. The bottom inset shows a scanning electron microscope (SEM) image of the assembled film. Scale bar, 2 pm. The ZnO microparticles were synthesized using a low-temperature solution process. With reference to Fig. 22B, V ₀ (around 0 V) from thin film (around 10 pm thick) made from single-walled carbon nanotubes (SWCNTs) is depicted. The SWCNTs (#US4101 ; US Research Nanomaterials, Inc.), with diameters of 1 -2 nm similar to nanowire, yield molecular pores in the film but lack surface functional groups. The thin film was made by dropcasting SWCNTs solution prepared in dimethyl sulfoxide (DMSO). With reference to Fig. 22C, V ₀ (around 0 V) from thin film (around 10 pm thick) made from polyvinylpyrrolidone (PVP) is depicted. The PVP thin film is hygroscopic and adsorbs similar amount of moisture (e.g., 30 w.t.%) in the ambient environment. The film was made by dropcasting PVP solution (3 mg/mL, molecular weight 360000) onto the bottom electrode. With reference to Fig. 22D, V ₀ (around 0 V) from thin film (around 10 pm thick) made from potassium chloride (KCI) by evaporating KCI solution is depicted. Moisture adsorption in hygroscopic KCI will result in ionic conduction.

Open-circuit voltage (Fig. 23A) and short-circuit current (Fig. 23B) measured from a thin film made from genetically modified nanowire (Aro-5) in the ambient environment (RH around 50%). In Aro-5 nanowire, the four aromatic amino acid groups in the pilin monomer are substituted with alanine. The substitutions nevertheless do not alter the molecular structure in the nanowire.

Previous measurements of individual nanowires revealed that the Aro-5 nanowire had over 100-fold lower conductivity compared to a wild-type wires, which characterized the intrinsic electron conduction. When nanowires aggregate into thin films, the measured conductivity will include extrinsic conduction through the nanowire-nanowire interface (e.g., contact resistance). The dominant nanowire-nanowire contact resistance was the reason why the measured conductivity in nanowire films (e.g., ~pS/cm) was over 10 ³ fold lower than that of individual nanowires (e.g., ~mS/cm). It was also the main reason why a wild-type nanowire film had only several times (e.g., 3-10) higher conductivity than Aro-5 nanowire films, as the extrinsic conduction (a limiting factor) basically screened the intrinsic conduction.

Similarly, the extrinsic conduction will dominate in thin films. As a result, Aro-5 thin films will have a conductivity closer to wild-type one. This is consistent with the result that the Aro-5 films produced a similar voltage but a around 4-fold lower current (around 80 nA) compared to wild-type device. This 4 ^c reduction in conductance falls into the range (e.g., 3-10) observed in nanowire films.

Electric outputs in nanowire film prepared from close-to-neural solution (pH around 8). Previous study revealed that a low pH (around 2) in the nanowire preparation solution increased the conductivity in individual nanowire, although the mechanism is not yet known (e.g., by doping to functional groups).

For this reason, hydrochloric acid (HCI) was added to adjust the pH in nanowire preparation solution to around 2 and intend to improve nanowire film conductivity. As the film was formed by evaporating the solution at 80 °C (see Materials and Methods), the volatile HCI component was expected to be driven out and introduce negligible effect to observed phenomenon. With reference to Fig. 24A, as control, thin-film device made from as-purified nanowire solution (e.g., pH around 8) without adding HCI produced similar open-circuit voltage (Vo around 0.5 V) in the ambient environment (RH around 45%), which is consistent with the expectation because voltage generation is diffusion based and hence only dependent on film/nanowire structure. With reference to Fig. 24B, the reduced short-circuit current (/ _sc around 120 nA) is consistent to the circuit analysis that an increase in film resistance leads to reduced current. The nanowire film had an increased resistance (by a factor around 2) compared to film prepared at pH around 2.

Open-circuit voltage ( V ₀ around 0 V) from control devices added with HCI. HCI solution (pH around 2) was purposely added to thin-film devices made from other materials and left dry. Measurements showed negligible Vo (e.g., less than 1 mV) in devices made from SWCNTs (Fig. 25A) and hygroscopic PVP (Fig. 25B) in the ambient environment (RH around 50%).

Reversible current output from a nanowire device with respect to the change in relative humidity (RH). With reference to Fig. 26, a load resistor ( RL =

2 MW) was added to the circuit as shown in the schematic (inset). The result shows the dominant role of ambient moisture plays for electric output.

Internal resistance scaling in nanowire devices. With reference to Fig.

27 A (left panel), a schematic of the device structure used for voltage/current scaling study is depicted. The width of the top electrode was kept constant (around 0.5 mm), whereas the sizes of the bottom electrode and nanowire film were changed. With reference to the right panel of Fig. 27 A, top-view current distribution in the nanowire device simulated by using the finite element method (COMSOL 4.3) is depicted. The square and rectangular bar (black lines) indicate the bottom and top electrodes, respectively. A thickness of around 5 pm and a sheet resistance around 1 MW/D in the nanowire film obtained from experimental values were used for the simulation. Note that eventually the actual values were less relevant as we focused on the change in relative resistance. Both top and bottom electrodes were assumed to be ideal conductors, given that the conductivity in gold electrodes (e.g., 4x10 ⁵ S/cm) is orders of magnitude larger than that in nanowire film. With reference to Fig. 27B, changes in resistance in the nanowire devices with respect to changes in device size from (upper curve) experiment (/. e. , V ₀ //sc) and (lower curve) simulation, respectively, are depicted. The resistance was

normalized to the (maximal) value obtained in the smallest device size (1 mm ² ). Estimate of the upper limit in power output. With reference to Fig. 28, the proposed mechanistic picture can help to estimate the theoretical limit in power output from the device. The possible maximal energy input from ambient moisture is P = DE x n, where AE, n are the average electron energy difference between ambient water molecules and the nanowire film, and water-molecule exchange rate (cnr ² -s- ¹ ). AE (around 0.2 eV) can be estimated from the voltage difference between an open circuit (around 0.5 V) and close circuit (around 0.3 V).

Meanwhile, the water resorption rate was experimentally determined in a dry nanowire film (around 1 pm thick). The QCM measurement showed that the dry film (size A around 0.20 cm ² ) adsorbed Am around 1.6 pg of water in t ~70 s (RH around 50%). The resorption rate {n’) can be calculated as:

where Mmo (18 g-mol ^-1 ) and A/A (6.022 x10 ²³ mol ^-1 ) are the molar mass of water and Avogadro's number, respectively. The equation yields a resorption rate n’= 3.9*10 ¹⁵ cm ^-2 · S ¹ .

In a general chemical/recombination process defined as [A]+[B]< [AB], the recombination rate (r) is proportional to the product of [A] and [B] as r=k [A] [B], whereas the dissociation rate (d) is proportional to [AB] as d=k [ AB] In this case, [A], [B], and [AB] are the densities of ambient water molecules, vacant sites on protein nanowires, and filled sites, respectively. [A] is considered constant. The resorption rate {n’) is the difference between recombination and dissociation as n’=r-d=k [A] [B]-k [AB]. During resorption, the number of vacant sites on

nanowires [B] is maximal whereas the water-filled sites are minimal (e.g., [AB]~0). Consequently, the resorption rate is approximately the same as recombination rate as n’~ /f [A] [B] At equilibrium (n - 0; or r=d), the number of vacant sites [B’] reduces. The exchange rate is the same as recombination rate (or dissociation rate) of /c [A] [B’], which is smaller than the initial resorption rate of /c [A] [B].

The above analysis indicates that the resorption rate {n’) can be viewed as the upper limit of the exchange rate n. Together, we can estimate the theoretical limit of power generation as P = AE x n ~ 120 pW/cm ² . The measured maximal electric output (around 20 pw/cm ² ) from the nanowire device was ~16% of the theoretical limit.

Electric output in nanowire device placed in an air gap. With reference to Fig. 29A, a schematic of the measurement setup is depicted. The air gap (around 20 pm) was controlled by defining the height of the supports (around 20 pm thick polyethylene-terephthalate films) to a top silicon substrate (cover). The nanowire device (around 0.5x0.5 cm ² ) had a film thickness around 10 pm. The top electrode was made by depositing Au layer (100 nm) on a polyimide substrate (around 1.2 pm thick). With reference to Fig. 29B, measured Vo and /sc from the device in the ambient environment (RFI around 55%) is depicted, showing similar value to that in open air.

Voltage output from connected nanowire devices in series. With reference to Fig. 30, an output voltage V ₀ around 10 V was produced by

connecting 17 nanowire devices (each with film thickness around 7 pm) in series in the ambient environment (RFI around 50%).

Charing to capacitor using nanowire devices. With reference to Fig. 31 , the capacitor’s voltage gradually increased to the open-circuit voltage (around 0.5 V) of a nanowire device in the ambient environment (lower curve, RFI around 60%), indicating the continuous energy input (charging) to the capacitor from the nanowire device. Multiple (4 ^c ) nanowire devices can be connected in series to charge the capacitor to higher voltage around 2.2 V (upper curve). This is also a direct evidence of the scalability in power output.

Ge-Si nanowire transistor and performance. With reference to Fig. 32A, a schematic of the Ge-Si core-shell nanowire transistor is depicted. The S, D and G denote source, drain and gate electrodes, respectively. The right panel shows a dark-field optical image of the fabricated nanowire transistor. Scale bar, 1 pm. With reference to Fig. 32B, a typical transfer curve from the transistor powered by external voltage Vds = 1 V is depicted. With reference to Fig. 32C, a schematic of using a protein-nanowire device to power the Ge-Si nanowire transistor is depicted. With reference to Fig. 32D, the source-drain current (Ids) at different gate voltages ( V _gs ) measured from the transistor is depicted. The non-zero I s at Vds = 0 indicates the powering from the protein-nanowire device. Note that the ON current in the protein nanowire-powered transistor was lower due to both a lower output voltage from the protein-nanowire device ( e.g ., around 0.5 V) and increased circuit resistance contributed from the internal resistance of the protein-nanowire device (e.g., around 2 MW).

Materials and Methods:

Synthesis and purification of protein nanowires. Geobacter

sulfurreducens (GS) was routinely cultured at 25°C under strict anaerobic conditions (80/20 N2-CO2) in chemostats in the previously described mineral based medium containing acetate (15 mM) as the electron donor and fumarate (40 mM) as the electron acceptor. Cells were collected with centrifugation and re- suspended in 150 mM ethanolamine buffer (pH 10.5). The nanowires were harvested and purified. Briefly, protein nanowires were sheared from the cells in a blender. Cells were removed with centrifugation. The nanowires in the supernatant were precipitated with ammonium sulfate followed by centrifugation. The precipitate was re-suspended in ethanolamine buffer and additional debris was removed with centrifugation. The nanowires were collected with a second 10% ammonium sulfate precipitation and subsequent centrifugation at 13,000 g. The nanowires were re-suspended in ethanolamine buffer. This nanowire preparation was dialyzed against deionized water to remove the buffer and stored at 4° C.

Fabrication of protein-nanowire devices. The bottom electrode (Cr/Au,

10/100 nm) was first defined on a glass slide (25x75 mm ² , Fisher Scientific) by standard metal electron-beam evaporation using a shadow mask. A

polydimethylsiloxane (PDMS, Sylgard 184, 10:1 mix ratio; Dow Corning) film (3-5 mm thick) was cut with an opening (1 -25 mm ² ), which served as the well for holding nanowire solution and placed on the glass slide with the opening aligned to the defined bottom electrode. The purified nanowire solution was tuned to pH 2.0 by hydrochloric acid (HCI) solution to improve nanowire conductivity and

dropcasted into the PDMS well. Nanowire film prepared by as-purified, close-to- neutral solution without HCI yielded similar electric output. The glass slide was then placed on a hot plate (around 80 °C) to facilitate solvent (water) evaporation to form nanowire thin film. Note the nanowires were revealed to be stable at temperature >100 °C. The final nanowire-film thickness was controlled by tuning the solution volume over unit area. Empirically, 110 pL/cm ² nanowire solution (150 pg/mL) yielded an average film thickness around 1 pm. The PDMS mold was removed after nanowire-film assembly. Finally, a confined gold electrode was placed on top of the nanowire film to complete the device structure for electrical measurement. Two forms of top gold electrodes were used. The first was a braided gold-plated shield (around 0.7 mm diameter, model CC-SC-50; LakeShore) and the second was a polyethylene terephthalate (PET) thin-film stripe (around 0.5 mm wide) coated with 50-nm gold film. Both top electrodes yielded close electrical outputs. For control protein-nanowire devices using printed carbon electrodes, conductive carbon film was printed using a desktop inkjet printer (DMP-2831 , Dimatix; carbon ink: JR-700FIV, NovaCentrix) on the glass slide and on a paper stripe to form the bottom and top electrodes, respectively.

Fig. 33A-G depicts the device fabrication and structure. With reference to Fig. 33A, a schematic of device fabrication is depicted. Specifically, in step I, purified nanowire solution (150 pg/mL) was first dropcasted on top of a defined Au bottom electrode by using a molded PDMS well. In step II, the device was then placed on a hotplate (around 80 °C) to facilitate the solvent (water) evaporation to (in step III) form nanowire thin film. In step IV, a confined top Au electrode was placed on the dry nanowire film to form the device. Fig. 33B depicts a scanning electron microscopy (SEM) image of a typical nanowire thin film prepared. Scale bar, 10 pm. Fig. 33C depicts a transmission electron microscopy (TEM) image of the nanowire film at relatively high density. Note that nanowire density in actual thin-film devices (4-7 pm thick) can be higher but was less transparent for TEM imaging. For comparison, TEM images of nanowire networks at low density (Fig. 33D) and medium density (Fig. 33E) are depicted. Scale bars, 100 nm. Fig. 33F depicts a photo image of an as-fabricated nanowire device array on a glass slide with different bottom -electrode sizes (e.g., 1 , 4, 9, 16, 25 mm ² ). The top electrodes had not yet been placed on. Scale bar, 5 mm. Fig. 33G depicts typical nanowire devices using (top panel) braided gold-plated wire or (bottom panel) gold-coated PET stripe as the top electrodes. Scotch tape (outside the nanowire-film regime) was used to mechanically fix the top electrodes. Scale bars, 5 mm.

Figs. 34A-B depict control devices using carbon electrodes. With reference to Fig. 34A, the open-circuit voltage ( ₀ ) was recorded from a nanowire device using a pair of top and bottom carbon electrodes in the ambient environment (RFI around 50%). V ₀ shows a stable average value around 0.5 V. The top and bottom carbon electrodes were printed on a paper stripe and glass slide, respectively (Inset). The brown dashed line delineates the nanowire film. The thickness of nanowire film was around 7 pm, and the size of the nanowire film was around 5x10 mm ² . With reference to Fig. 34B, to exclude possible side effect from contaminates in printed carbon electrodes, a pair of commercial glassy carbon electrodes was also used for the measurement. The open-circuit voltage ( Vo around 0.4 V) maintained in the ambient environment (RFI around 40%). The inset shows the measurement setup. A nanowire film (around 7 pm thick) was deposited directly on the bottom glassy-carbon electrode, whereas the top glassy-carbon electrode was shifted to the film edge to allow moisture exposure. The right panel shows the actual glassy-carbon electrode.

Synthesis of Germanium-Silicon (Ge-Si) core-shell nanowires. The Ge-

Si core-shell nanowires were synthesized by the Au-nanocluster-catalyzed vapor- liquid-solid method described previously. Specifically, a growth substrate (Si substrate with 600 nm thermal S1O2, Nova Electronics) was first dispersed with gold nanoparticles (10 nm, Ted Pella). Then the growth substrate was placed in a quartz-tube reactor. The Ge core was synthesized at 270 °C and 450 Torr, with 30 seem germane (GeFI ₄ , 10% in H2) and 200 seem H2 serving as the reactant and carrier gases, respectively. The growth time was around 1 hour, yielding Ge nanowires with an average length of around 50 pm and an average diameter 10 nm. The epitaxial Si shell was grown immediately after the growth of core at 460 °C and 5 Torr for 2 min, with 5 seem silane (SiFH ₄ ) as the reactant gas. The epitaxial growth yielded an average Si shell thickness around 2-3 nm, resulting in core-shell nanowires with an overall diameter around 15 nm. Fabrication of Ge-Si nanowire transistors. The Ge-Si nanowires were first dispersed in ethanol solution, assisted by a brief ultrasonication. Then the dispersed nanowires were dropcasted on a Si substrate coated with 600 nm S1O2 (Nova Electronics). The source and drain contacts of the nanowires were defined by standard electron-beam lithography, followed by the thermal evaporation of metal contacts (Cr/Ni, 1/40 nm) and lift-off process. A tri-layer Al203/Zr02/Al203 (2/5/5 nm) was deposited by atomic-layer deposition to serve as the top-gate dielectric. The top-gate contact was definition by standard electron-beam lithography, thermal evaporation of metals (Cr/Au, 4/65 nm), and liftoff process.

Electrical measurements. The electrical measurements were performed in ambient environment, unless otherwise specified. The output voltage ( Vo) in the nanowire devices was first buffered by a unit-gain amplifier (LM 741 ; Texas Instruments) and the short-circuit current (/ _sc ) was amplified with a preamplifier (DL-1211 ; DL Instruments). Both signals were then recorded at an acquisition rate of 10-100 Hz using a 16-channel A/D converter (Digidata 1440A; Molecular Devices) interfaced with a computer running recording software (pCIamp 11 ;

Molecular Devices). The reason to use a unit-gain amplifier (LM 741 ; Texas Instruments) for voltage-signal buffering is that the nanowire devices have an internal resistance ~MW, which is comparable to the input resistance of the A/D converter (around 1 MW), so a direct connection would induce measurement error. The RH in the ambient environment was recorded by using a humidity datalogger (R6030; REED Instruments). The current-voltage (/-V) sweep in the nanowire devices were performed by using a source meter (Keithley 2401 ; Tektronix) interfaced with computerized recording software. The transfer characteristics in the Ge-Si nanowire transistors were measured by using a semiconductor

characterization system (Keithley 4200-SCS; Tektronix). The sheet resistance in the nanowire film was measured by using a four-point resistivity system (Pro-4; Signatone). Individual capacitors (CAPXON Electrolytic Capacitors; 1000 pF 16 V) were charged by nanowire devices with average ~0.55 V voltage output. The LCD (ADM1602K-NSW-FBS/3.3 V; Sparkfun electronics) was lighted by ten capacitors in series and LED (630-HLMP-K150; Mouser electronics) was lighted by 4 capacitors in series.

Humidity control. For some specific device characterizations carried out at controlled RH, the RH was tuned through two approaches. First, carrier gases (e.g., N2, O2, air) bubbling through a water-containing conical flask was led into a gas-purge desiccator cabinet (H42053-0002; Bel-Art), and the flow rate was adjusted to control the RH in the desiccator cabinet. The RH was real-time monitored by a hygrometer (Model 8706; REED Instruments). The bubbler method was used for controlled RH in different gas environments and moisture adsorption measurements. Alternatively, RH was controlled by tuning the equilibrium vapor pressure of sulfuric acid solutions, i.e., the concentration of sulfuric acid. The relationship between the concentration of sulfuric acid and (measured) RH is listed below. The equilibrium-vapor method was used for control of stabilized RH over long term, instant RH changes, and wide-range RHs.

Imaging. The thicknesses in protein-nanowire films were measured by a desktop scanning electron microscope (SEM, EM-30 Plus; Element Pi). The optical image of Ge-Si nanowire device was taken by using an upright microscope

(Olympus BH2-UMA). The nanowire networks were imaged by using a

transmission electron microscope (TEM, JEM-2200FS; JEOL). The bonding spectra in protein nanowires were performed by a Fourier-transform infrared spectroscopy (FTIR; Perkin Elmer) equipped with a universal attenuated-total- reflection (ATR) sampling accessory. Molecular dynamics simulation. Atomistic MD (molecular dynamics) simulations of the protein nanowires were performed using the CHARMM program using the latest CHARMM 36m force field. The initial structure was obtained from a previous modeling work. 12 monomers were included in this work, which is sufficient to provide intact filament environment for flexible C-terminal tails (Cter) of the first six monomers. Two simulations were performed in this work, one with the pilus filament in the vacuum phase (which mimics the fully dehydrated state), and the other one in solution phase (which mimics the fully hydrated state). For the pilus filament in vacuum, all Glu, Asp, Lys, and Arg residues were simulated in their neutral states. For the solution simulation, the filament was placed in a rectangular simulation box, solvated by 25,721 water molecules along with 24 K ⁺ ions to provide a neutral net charge of the system. The size of the simulation box was 21 x 7.5 ^c 7.3 nm ³ and periodic boundary conditions were imposed. Both systems were first energy minimized for 1000 steps using a steepest descent algorithm, and another 1000 steps using the adopted basis Newton Raphson method. The systems were then heated from 100 K to 300 K in 10 ps, during which all heavy atoms were retrained using harmonic potentials with force constants of 20 kcal/mol/A ² . This was followed by additional 1 ns simulation where the restraint force constant was reduced to 0.2 kcal/mol/A ² . In production simulations, the backbone heavy atoms of residues 4-50 were restrained by harmonic potentials with force constants of 0.2 kcal/mol/A ² , to maintain the filament core structural model. The solvated system was simulated under NPT conditions at temperature of 300 K and pressure of 1 atm. Van der Waals interactions were truncated at 1.3 nm, with the force smoothly switching to zero starting from 1.2 nm. Long-range electrostatic interactions were calculated using the particle mesh Ewald method. Lengths of all hydrogen-containing bonds were constrained using the SHAKE algorithm, and the MD integration time step was 2 fs. The vacuum simulation was performed at 300 K with similar setups as used in solution. Both simulations lasted for 110 ns, with the first 10 ns trajectories discarded in the analysis.

Atomistic molecular modeling and simulations were performed to further examine the nanoscale water permeable pores that may be formed in a nanowire network. Inspired by the TEM images, parallel configurations where the filaments would achieve the tightest packing were primarily focused on. 588 simulations were performed, in which the relative position of these two filaments were shifted along two directions, parallel or perpendicular to the filament axis, and one of the filaments was rotated along the filament axis. One filament was defined as the reference filament, and the other filament was mobile. 21 windows were set up along the direction of the filament axis, with the relative shift of two filaments ranging from -4 to 4 nm with a spacing of 0.4 nm. At each shift along the filament axis, four windows were used along the direction perpendicular to the filament axis, with the relative distance between two filaments varied between 3.3 and 4.2 nm with an interval of 0.3 nm. Seven windows were used for the rotation of one filament, with rotation angles between 0 and 60° with an interval of 10°. At each window, MD simulations were performed to equilibrate inter-filament interfacial packing. During MD equilibration, all Ca atoms of the helical core segment

(residues 4-50) were fixed, in order to maintain the integrity of both filaments and minimize modelling error due to undesired structural changes. Each system was first energy minimized for 2000 steps, and then slowly heated up from 100 K to 300 K in 5000 steps. Production simulations were performed under 300 K for 3 ns. During analysis, the first half of each trajectory was discarded as the equilibration process, and the averaged potential energy was computed for each window. This allowed one to identify the inter-filament distance and filament rotation with minimal averaged potential energy for each shift distance along the filament axis. The maximum enclosed pore was then analyzed using the HOLE program ¹⁴ for the most stable configuration identified at each shift along the filament axis.

Similar approaches were also used to examine the formation of water- permeable pores in OmcS-OmcS filaments and OmcS-p/7/ filaments. In both cases, one OmcS filament was defined as the reference filament, and the other filament was mobile. 21 windows were set up along the direction of the filament axis, with the relative shift of two filaments ranging from -10 to 0 nm with a spacing of 0.5 nm. Since OmcS filament showed a sinusoidal shape with a period of around 20 nm, the pore radii as a function of their relative shift in this direction will be symmetric with respect to relative shift of 0 nm. At each shift along the filament axis, six windows were used along the direction perpendicular to the filament axis, with the relative distance between two filaments varied between 4.2 and 5.7 nm with an interval of 0.3 nm in this direction. In the system of OmcS-OmcS filaments, nine windows were used for the rotation of one filament, with rotation angles between 0 and 80° with an interval of 10°. In the system of OmcS-p/7/ filaments, seven rotational windows were used with the rotation angles ranging from 0 to 60° with a spacing of 10°. At each window, 2000 steps of energy minimization were performed to remove any steric clashes, and the final structure was analyzed using the HOLE program to identify water-permeable pores. At each shift along the filament axis, only results from the structure with minimal energy were reported, since this configuration was considered most probable.

Although the invention has been shown and described with respect to a certain embodiment or embodiments, it is obvious that equivalent alterations and modifications will occur to others skilled in the art upon the reading and

understanding of this specification and the annexed drawings. In particular regard to the various functions performed by the above described elements (components, assemblies, devices, compositions, etc.), the terms (including a reference to a "means") used to describe such elements are intended to correspond, unless otherwise indicated, to any element which performs the specified function of the described element (i.e., that is functionally equivalent), even though not structurally equivalent to the disclosed structure which performs the function in the herein illustrated exemplary embodiment or embodiments of the invention. In addition, while a particular feature of the invention may have been described above with respect to only one or more of several illustrated embodiments, such feature may be combined with one or more other features of the other embodiments, as may be desired and advantageous for any given or particular application.