Patent Application: US-37620907-A

Abstract:
lithographically patterned nanowire electrodeposition combines attributes of photolithography with the versatility of bottom - up electrochemical synthesis . photolithography is employed to define the position of a sacrificial nanoband electrode , preferably formed from a metal such as nickel , copper , silver , gold or the like , which is stripped using electrooxidation or a chemical etchant to advantageously recess the nanoband electrode between a substrate surface and the photoresist to form a trench defined by the substrate surface , the photoresist and the nanoband electrode . the trench acts as a “ nanoform ” to form an incipient nanowire during its electrodeposition . the width of the nanowire is determined by the electrodeposition duration while its height is determined by the height of the nanoband electrode .

Description:
embodiments described herein are directed to a method of lithographically patterned nanowire electrodeposition ( lpne ) for preparing metal nanowires and patterning these nanowires over large areas of the surface of an insulator such as glass , oxidized silicon or the like . as depicted in fig1 , the lpne process 10 involves the preparation of a sacrificial nanoband electrode 14 , formed of nickel , copper , silver , gold or other metals , using optical lithography , and the subsequent electrodeposition at the sacrificial nanoband electrode 14 of a metal nanowire 20 , preferably formed of a noble metal such as gold , platinum or palladium ( au , pt , or pd ) but may include other metals , such as , cadmium , bismuth and the like or metalloids , such as , e . g ., silicon , germanium and the like . the nanoband electrode 14 is preferably recessed between the surface of the insulator 12 and a photoresist layer 16 forming a trench 18 defined by the surface of the insulator 12 , the electrode 14 and the photoresist 16 . the electrodeposition of a nanowire 20 into this “ nanoform ” produces a wire 20 with a generally rectangular cross - section where the height and width are independently controllable as a function of trench height and electrodeposition duration within a precision of about 5 nm , down to about 20 nm in width and 6 nm in height . since optical lithography is used to define the position of the nanowires 20 on the surface of the insulator 20 , the spacing between nanowires 20 is constrained by the optical diffraction limit . the lpne process 10 shown in fig1 is described in greater detail as follows with regard to an example of an implementation of the process . one of skill in the art will readily recognize that the materials used were chose for exemplary purposes only . the lpne process 10 was implemented as follows : soda lime glass microscope slides were cleaned in aqueous nochromix solution , air dried , and diced into 1 ″× 1 ″ glass squares 12 . onto each glass square 12 , a nickel film 14 ( espi , 5n purity ), 20 - 100 nm in thickness , was deposited by hot filament evaporation at a rate of 0 . 5 - 1 . 5 å s − 1 ( step 1 ). the film thickness and evaporation rate were monitored using a quartz crystal microbalance ( sigma instruments ). the nickel film - covered glass squares were then coated with a positive photoresist layer 16 ( shipley 1808 ) by spin coating ( step 2 ). this involved the deposition of about a 1 ml aliquot of photoresist onto each square and the rotation of the square at about 2500 rpm for 40 s . this produced a photoresist layer 16 having a thickness ( after soft baking ) of about 1 um . the freshly coated squares were soft - baked at about 90 ° c . for 30 minutes . after cooling to room temperature , a transparent contact mask ( not shown ) was pressed onto the photoresist 16 with a quartz plate ( not shown ) and the masked surface was exposed to uv light having a wavelength of about 365 nm and output power of about 0 . 5 mw cm 2 for 2 minutes . to remove unexposed portions of the photoresist 16 and expose the nickel layer 14 , the slide was then soaked first in a developer / water solution ( 1 part shipley mf - 351 to 4 parts water ) for 20 s , and then in pure water for 1 minute , before drying in a stream of ultra - high purity ( uhp ) n 2 ( step 3 ). the exposed nickel 14 was then electrochemically removed ( step 4 ) and palladium , platinum , or gold 20 was electrodeposited ( step 5 ) onto the nickel nanoband electrodes 14 produced by this process . the electrochemical stripping of the nickel layer 14 and the electrodeposition of these metals 20 was carried out in a 50 ml , one compartment , three - electrode cell . nickel dissolution was carried out in aqueous 0 . 1 m kcl containing 0 . 1 ml of concentrated hcl . palladium was electroplated from an aqueous solution containing 2 mm pd ( no 3 ) 2 , 2 mm saccharine , and 0 . 1 m kcl . platinum was electroplated from a solution containing 0 . 1 m kcl , and 1 . 0 mm k 2 ptcl 6 at 0 . 025 v vs . sce . gold was electroplated from aqueous commercial gold plating solution ( clean earth solutions , carlstadt , n . j .— a 6 mm aucl 3 solution ), with added 1 . 0m kcl at − 0 . 90 v vs . sce . all aqueous solutions were prepared using millipore milliq water ( σ & gt ; 18 . 0 m cm ). a saturated calomel reference electrode ( sce ) and a 2 cm 2 pt foil counter electrode were also employed . the stripping and deposition were both carried out on a computer - controlled eg & amp ; g 273a potentiostat / galvanostat . the removal of the sacrificial metal ( nickel , silver , copper , gold , or the like ) layer can be accomplished using either electrooxidation or chemical etching . as one preferred embodiment , the stripping of the nickel layer 14 is achieved by securing the photoresist 16 — covered nickel film 14 with self - closing metal tweezers , and placing part of the exposed nickel film 14 in the nickel stripping solution . the film 14 was then held at a potential of − 0 . 085 v vs . sce for 1000 s . this removed all of the exposed nickel 14 and produced an “ undercut ” beneath the photoresist 16 at each edge of the nickel layer 14 produced by photolithography on the surface . the slide was then rinsed with nanopure water , and placed into the palladium deposition solution . palladium metal 20 was electrodeposited by holding the nickel film 14 at a potential of about + 0 . 225 v vs . sce for times ranging from about 25 to 400 s . the glass slide 12 was then rinsed with nanopure water and dried with uhp n 2 . the photoresist 16 was then removed ( step 6 ) by rinsing the slide with electronic grade acetone ( acros ), methanol ( fisher ), then nanopure water , respectively , before drying with uhp n 2 . the excess nickel film 14 was then removed by washing with dilute hno 3 ( step 7 ). the position of the nanowires 20 on a surface of an insulator 12 such as glass is determined by the position of the nanoband electrodes 14 prepared in the first four steps of the lpne process 10 shown in fig1 . in fritsch et al ., individually addressable , submicrometer band electrode arrays ; fabrication from multilayered materials ; analytical chemistry 70 , 2902 - 2907 ( 1998 ), gold nanoband electrodes were prepared using a process similar to the first four steps shown in fig1 , but lacking in the formation and use of a trench 18 as described and illustrated herein . the process 10 depicted in fig1 advantageously removes exposed nickel or other nanoband electrode material 14 electrochemically at step 4 by applying an oxidizing potential to the material , which for nickel is in the range from about − 0 . 085 to − 0 . 10 v vs . sce ( see fig2 a ). oxidation is continued until the electrode material 14 at the exposed edges 15 of the pattern is etched , preferably undercutting the photoresist 16 by about 100 - 300 nm ( fig2 a ). three transients are shown in fig2 a for nickel layers 14 with approximate thicknesses of 40 nm , 70 nm , and 90 nm . for nickel films of these thicknesses , as shown , the etching current is approximately proportional to the nickel film thickness as the electrochemical undercutting occurs . “ over - etching ” of the material produces a trench 18 , horizontally oriented in this instance , into which a metal nanowire 20 can be electrodeposited in step 5 of fig1 . a recessed nickel nanoband 14 is both electrochemically reactive and accessible to redox species . to confirm this , the cyclic voltammetry of ru ( nh 3 ) 6 3 + , a metal complex , which undergoes a fast , reversible one electron reduction , was investigated . before dissolution of the exposed nickel , as shown in fig2 b , the cyclic voltammogram shows current peaks and hysteresis of the forward and reverse scans ; all consistent with the planar diffusion of this molecule to the relatively large nickel areas exposed by the dissolution of photoresist after lithography . after electrooxidation of the nickel and the formation of the horizontal trench , as shown in fig2 c , the ru ( nh 3 ) 6 3 + reduction current was reduced by a factor of more than 100 and a steady - state , sigmoidal cv showing no hysteresis was observed , qualitatively as expected for a nanoband electrode . this result demonstrated that the recessed nickel electrode was both electrochemically active and accessible to the dissolved redox species ru ( nh 3 ) 6 3 + , as required for nanowire electrodeposition . the growth of the nanowire 20 into the trench 18 occurs in three phases as shown in fig3 . first , a plating voltage for a metal nanowire material 20 such as , e . g ., palladium , is applied to an aqueous solution containing 2 mm pd ( no 3 ) 2 , 2 mm saccharine , and 0 . 1 m kcl and immediately after the application of a plating voltage the current increases as the palladium nucleates along the entire length of the nickel nanoband electrode 14 . when this nucleation process was complete , a quasi - constant deposition current was observed during growth of the confined metal nanowire 20 because the wetted surface area of the confined wire 20 is constant , and because for such a kinetically - controlled reaction , the deposition current per unit area of the metal is constant . the quasi - constant current seen from 20 to 50 seconds is seen because for this kinetically - controlled deposition process current is proportional to the wetted surface area which remains constant while growth of the nanowire 20 is confined to the horizontal trench 18 . terminating growth during this phase results in a nanowire 20 having a rectangular cross section , such as seen in fig3 b . if wire growth is continued , deposited metal fills the trench 18 and begins to emerge from it and the total current increases because the wetted surface area increases . this “ blooming ” 21 of the nanowire 20 as it emerges from the trench is undesirable since it produces a distribution of dendrites along one edge of the nanowire as shown in fig3 c . the nanowires 120 produced by the lpne process 10 shown in fig1 have , as depicted in fig5 a , an approximately rectangular cross section that is enforced by the dimensions of the trench 18 . the minimum dimensions for the width and height of these nanowires is about 40 nm and 20 nm , respectively . for example , a platinum nanowire 220 shown in the sem image of fig4 a is 46 nm in width , 39 nm in height and 1 cm in length . as shown in fig4 b - d , large substrate areas exceeding 1 cm 2 can be lithographically patterned with nanowires ; i . e ., ( b ) parallel gold nanowires 320 , 1 cm in length and spaced by 9 μm ; ( c ) a coiled nanowire 420 with total length of 2 . 7 cm ; and ( d ) nanowire loops 520 . the nanowires produced show remarkable dimensional uniformity over the entire sample surface . the relative standard deviations of the nanowire width and height were about 10 - 12 % and & lt ; 5 %, respectively , for the patterns shown in fig4 b - d . of particular interest is the fact that corners , like those present in the pattern of the nanowire 420 shown in fig4 c , do not cause either narrowing or thickening of the nanowire — the latter expected for a diffusion - controlled deposition processes . this curvature invariance of the wire width is expected if the wire electrodeposition reaction occurs under conditions of kinetic , not diffusion , control . the width and height of these nanowires can be independently controlled as a function of electrode thickness or trench height and electrodeposition duration . the electrode layer thickness fixes the height of the nanowires while the width of the nanowires is proportional to the duration of the electrodeposition step . this control is documented by the data shown in fig5 b and 5 c . the afm - measured nanowire height increases linearly with the nickel layer thickness for nanowires composed of gold , palladium and platinum ( fig5 b ). the slope of these data points is 0 . 98 indicating that the nanowire height equals the thickness of the evaporated nickel layer . the smallest attainable nanowire heights were in a range of about 18 nm for au and pt and somewhat larger for pd . for a metal electrodeposition process occurring within a rectangular trench at a time - invariant current density , j dep , the width of the deposited nanowire , w , is given by : w ( t )= j dep t dep v m / nf ( 1 ) where t dep is the deposition time , v m is the molar volume of the deposited metal , n is the number of electrons required to reduce each metal complex ion , and f is the faraday constant ( 96485 c eq . − 1 ). plots of w versus t dep for gold , palladium and platinum ( fig5 c ) are all approximately linear in accordance with eq . 1 . the slopes of these plots are proportional to j dep the magnitude of which depends on the concentration of metal complex present in the plating solution and on the electrodeposition potential . previous measurements of the electrical properties of metal nanowires have employed wires ranging in length from 500 nm to 5 μm . using a four - point probe shown in fig6 a ( inset ), we measured the electrical behavior of 4 . 00 μm long sections of two gold nanowires with cross - sections of 20 nm × 233 nm , and 100 nm × 166 nm . two characteristics of metallic conduction are seen in these nanowires : first , the current voltage behavior was ohmic ( fig6 a ) and second , a positive temperature - coefficient of resistivity , α , was observed ( fig6 b ). however clear quantitative differences in the behavior of these nanowires , associated with their diminutive size , are also seen . the measured room temperature electrical resistivity of these nanowires was significantly higher than expected for bulk gold , and this disparity increased with decreasing temperature , down to 10k , just as reported for nanowires in several previous studies 14 - 18 . one well - understood source for the elevated electrical resistivity of the nanowires is boundary scattering : an increased frequency for the inelastic collision of conduction electrons with wire surfaces . but the contribution of boundary scattering to the total resistivity of our 20 nm nanowires , as estimated using fuchs - sondheimer theory , is approximately a factor of 2 in resistivity for the 20 nm nanowire and this enhancement is temperature independent . two additional contributing factors are impurities in the electrodeposited gold , and a mismatch in the coefficients of thermal expansion for gold ( κ = 14 × 10 − 6 k − 1 , 300k ) and the soda lime glass support ( κ = 9 × 11 − 6 k − 1 , 300k ). this mismatch , which increases with decreasing temperature , means that the length of the gold nanowire shrinks more rapidly with decreasing temperature than the glass surface on which it is supported , placing it in tension . the total strain that accumulates in cooling from 300k to 80k , for example , is significant : approximately 0 . 7 μm for the 400 μm nanowires investigated here . while the invention is susceptible to various modifications , and alternative forms , specific examples thereof have been shown in the drawings and are herein described in detail . it should be understood , however , that the invention is not to be limited to the particular forms or methods disclosed , but to the contrary , the invention is to cover all modifications , equivalents and alternatives falling within the spirit and scope of the appended claims . 1 . spicer , d . f ., rodger , a . c . & amp ; 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