Deaggregated electrically conductive polymers and precursors thereof

Abstract: Deaggregated substituted and unsubstitued polyparaphenylenes, polyparaphenylevevinyles, polyanilines, polyazines, polythiophenes, poly-p-phenylene sulfides, polyfuranes, polypyrroles, polyselenophene, polyacetylenes formed from soluble precursors and combinations thereof and copolymers thereof and methods of fabrication are described. The deaggregated polymer molecules when subsequently doped show higher electrical conductivity. Agents such as lithium chloride, m-cresol and nonylphenol are used to deaggregate the polymer molecules. The deaggregating agents can be added prior to or during doping the molecules.

Description: FIELD OF THE INVENTION The present invention is directed to methods of fabrication of electrically conducting polymers having enhanced electrical conductivity. In particular, the present invention is directed to methods to deaggregate electrically conductive polymers and precursors thereof. BACKGROUND OF THE INVENTION Electrically conductive organic polymers have been of scientific and technological interest since the late 1970's. These relatively new materials exhibit the electronic and magnetic properties characteristic of metals while retaining the physical and mechanical properties associated with conventional organic polymers. Herein we describe electrically conducting polyparaphenylene vinylenes, polyparaphenylenes, polyanilines, polythiophenes, polyazines, polyfuranes, polypyrroles, polyselenophenes, poly-p-phenylene sulfides, polyacetylenes formed from soluble precursors, combinations thereof and blends thereof with other polymers and copolymers of the monomers thereof. In order for these materials to be used in place of metals in more applications, it is desirable to increase the conductivity of these materials. The article "The Concept of Secondary Doping as Applied to Polyaniline", A.G. MacDiarmid, A.J. Epstein, Synthetic Metals, 65 (1994), 103-116, describes increasing the electrical conductivity of a polyaniline by exposing a doped polyaniline to a secondary dopant, such as meta-cresol. MacDiarmid et al. teaches that the secondary dopant results in an intra-molecular conformational change in the polyaniline molecule. Prior to being exposed to the secondary dopant, the doped polyaniline molecule is in a compact coil intra-molecular conformation. Intra-molecular conformation refers to the conformation of a single molecule or a single polymer chain in which the molecular chain is coiled around itself. In contra-distinction inter-molecular structure refers to the structural arrangement of more than one molecule or polymer chain in which the molecules or chains are bonded together or coiled around each other forming aggregates. These aggregates are then comprised of many polymer chains intertwined or entangled. MacDiarmid et al. teaches that the secondary dopant causes a intra-molecular conformational change, i.e., the molecule or the chain unravels and assumes an expanded coil conformation. A film of this expanded coil polyaniline has enhanced electrical conductivity because of an increase in the crystallinity of the material formed from the aggregated straightened molecules. In the article "Transport studies of protonated emeraldine powder: A granular polymeric metal system", F. Zuo et al., Phys. Rev. B 36, 3475 (1987) it has been reported that the polyaniline which has been doped has electrically conductive regions or islands which are of the order of 20-30 nm (200-300Å). The spaces between these regions are significantly less electrically conductive. When an electrical current flows along the polyaniline molecules, current flows through the electrically conductive regions and hops over the less electrically conductive region to an adjacent electrically conductive region. According to "Polymer, 35 , 2902 (1994)" PANI is polymerized in the presence of DBSA which acts both as a surfactant and a dopant. Cast films thereof are said to exhibit conductivities of > 100 S cm -1 as a result of exhibiting more homogeneous protonation of the imine nitrogens. It is an object of the present invention to increase the electrical conductivity of electrically conductive polymers. It is another object of the present invention to enhance the electrical conductivity of an electrically conductive polymer by deaggregating aggregated molecules which are precursors of the electrically conducting polymers so that the molecules can be more uniformly doped. It is another object of the present invention to deaggregateìè polymer molecules prior to being doped to the electrically conducting state. It is another object of the present invention to lower the glass transition temperature of the precursor to an electrically conductive polymer and of an electrically conductive polymer by the addition of deaggregating agents. It is another object of the present invention to increase the electrical conductivity of electrically conductive polymers by extending the electrically conductive regions or islands of the electrically conductive polymer. Electrical conductivity of a deaggregated electrically conductive polymer can be further increased by stretch orientation. The shelf-life of a precursor to an electrically conductive polymer and of an electrically conductive polymer can be increased by the addition of deaggregating agents. SUMMARY OF THE INVENTION A broad aspect of the present invention is an electrically conductive polymer having electrically conductive regions having a dimension greater than about 300Å. Another broad aspect of the present invention is a precursor to an electrically conductive polymer containing a deaggregating agent, such as a complexing agent. In a more particular aspect of the present invention, the dimension of the electrically conductive regions are enhanced by a deaggregating agent. Another broad aspect of the present invention is a body of material containing precursor molecules to electrically conductive molecules wherein the body of material has regions of aggregated precursor molecules of less than about 100 nm. Another broad aspect of the present invention is a method for fabricating electrically conducting polymers, the electrical conductivity of which is enhanced by deaggregating the polymer either prior to being doped to the electrically conducting state or after being doped to the electrically conducting state. A more specific aspect of a method of the present invention is deaggregating the precursor polymer or electrically conducting polymer either in solution or in the solid state. Another more specific aspect of a method of the present invention includes steps of providing a first admixture of an additive in a solvent; forming a second admixture by dissolving in the first admixture precursor polymers to electrically conduct ing polymers wherein the additive deaggregates the precursor molecules and either adding a dopant to the second admixture to dope the precursor to the electrically conductive polymer or forming a film of the second admixture and then doping the film in the solid state. Another more specific aspect of a method of the present invention includes providing aniline molecules which are oxidatively polymerized in an acid solution in the presence of a deaggregating agent to result in a deaggregated polyaniline. Another more specific aspect of a method of the present invention includes the steps of providing aniline molecules which are oxidatively polymerized in an acid solution to form an electrically conducting polyaniline salt which is then neutralized to the base non-doped form and deaggregated upon exposure to a deaggregating agent. Another more specific aspect of a method according to the present invention includes neutralizing a polyaniline salt to the base form in the presence of a deaggregating agent. Another broad aspect of the present invention is a method of causing a doped electrically conductive polymer in a compact coil conformation to undergo a conformational change from a compact coil to an expanded coil conformation by exposing the doped polymer to salts and surfactants. BRIEF DESCRIPTION OF THE DRAWINGS Further objects, features, and advantages of the present invention will become apparent from a consideration of the following detailed description of the invention when read in conjunction with the drawing FIGs., in which: Fig. 1 is a gel permeation chromatograph (GPC) plot of polyaniline base in NMP which shows a bimodal distribution: a very high molecular weight component which is aggregated polyaniline molecules and a lower molecular weight peak. Fig. 2 shows a GPC plot of polyaniline base in NMP and 0.5 wt % lithium chloride which shows that the high molecular weight peak of Fig. 1 has been eliminated and the molecular weight of the other peak is actually higher. Fig. 3 is a general formula for a polyaniline. Fig. 4.1 is a general formula for a doped polyaniline. Fig. 4.2 is a general formula for the polysemiquinone radical cation form of doped polyaniline. Fig. 5 is a Dynamic Mechanical Thermal Analysis (DMTA) plot of polyaniline base film cast from 100% NMP. (First Run; ∼ 21% NMP remaining in film; under N 2 ; 2° C / min ) Fig. 6 is the DMTA plot (2nd run) of the same poylaniline film as shown in Fig. 5. This film has 0% NMP remaining in the film. The Tg is 251° C . Fig. 7 is a DMTA plot (2nd run) of polyaniline base which has been cast from 100% NMP doped with 1N HCl and undoped with 0.1 M NH 4 OH showing a Tg of 256°C. This film has ~ 2.8% NMP remaining in the film. Fig. 8 is a DMTA plot (2nd run) of polyaniline cast from NMP/.5 wt % LiCl showing a Tg of 180°C. Fig. 9 shows inter-molecular hydrogen bonding between undoped polyaniline molecules. Fig. 10 shows disruption of the intermolecular hydrogen bonding by a LiCl salt. Fig. 11 shows a schematic view of polyaniline molecules aggregated through inter-molecular hydrogen bonding. Fig. 12 shows a UV/VIS/near IR spectrum of polyaniline doped with an organic sulfonic acid in NMP showing a localized polaron peak. Fig. 13 shows the same plot as Fig. 12 but with 0.5 wt% LiCl added to the initial NMP solution from which the doped polyaniline was cast and shows a delocalization of the polaron peak. Fig. 14 shows the same plot as in Fig. 12, but with 1 wt% LiCl added to the initial NMP solution from which the doped polyaniline was cast and shows a significantly delocalized polaron peak. Fig. 15 is an atomic force micrograph of a polyaniline film cast ì fromìè 100% NMP showing clusters or bundles of polyaniline molecules of about 100 nm in size which are interpreted as aggregated regions. Fig. 16 is an atomic force micrograph of polyaniline film cast from NMP and subsequently exposed to m-cresol (Comparative example). Fig. 17 is an atomic force micrograph of the same material shown in Fig. 16 with the m-cresol pumped out (Comparative example). Fig. 18 is an atomic force micrograph of a polyaniline film cast ì from NMP and treated with 0.5 wt% nonylphenol showing deaggregation. Fig. 19 is an atomic force micrograph of a polyaniline film cast ì from NMP and treated with 0.5 wt% triton showing deaggregation. Fig. 20 is an atomic force micrograph of a polyaniline film cast from NMP and treated with 1.0 wt% nonylphenol showing more deaggregation than shown in Fig. 19. Fig. 21 schematically shows stretch orientation of a film to enhance electrical conductivity. DETAILED DESCRIPTION The present invention is directed to enhancing the electrical conductivity of substituted and unsubstituted polyanilines, which when doped, are electrically conducting. The general formula for these polymers can be found in U.S. Patent 5,198,153 to Angelopoulos et al. The substituted or unsubstituted polyaniline or copolymers of polyaniline has the general formula shown in Fig. 3 wherein each R can be H or any organic or inorganic radical; each R can be the same or different; wherein each R 1 can be H or any organic or inorganic radical, each R 1 can be the same or different; x ≥ 1; preferably x ≥ 2 and y has a value from 0 to 1. Examples of organic radicals are alkyl or aryl radicals. Examples of inorganic radicals are Si and Ge. This list is exemplary only and not limiting. The most preferred embodiment is emeraldine base form of the polyaniline wherein y has a value of approximately 0.5. In Fig. 4.1 polyaniline is shown doped with a dopant. If the polyaniline base is exposed to cationic species QA, the nitrogen atoms of the imine part of the polymer becomes substituted with the Q+ cation to form an emeraldine salt as shown in Fig. 4.1. Q+ can be selected from H+ and organic or inorganic cations, for example, ìè an alkyl group or a metal. QA can be a protic acid where Q is hydrogen. When a protic acid HA is used to dope the polyaniline, the nitrogen atoms of the imine part of the polyaniline are protonated. The emeraldine base form is greatly stabilized by resonance ì effects. The charges distribute through the nitrogen atoms and aromatic rings making the imine and amine nitrogens ì indistinguishable. The actual structure of the doped form is a delocalized polysemiquinone radical cation as shown in Fig. 4.2. The emeraldine base form of polyaniline is soluble in various organic solvents and in various aqueous acid solutions. Examples of organic solvents are dimethylsulfoxide (DMSO), dimethylformamide (DMF) and N-methylpyrrolidinone (NMP). This list is exemplary only and not limiting. Examples of aqueous acid solutions is 80% acetic acid and 60-88% formic acid. This list is exemplary only and not limiting. Fig. 1 shows a GPC (gel permeation chromatograph) of polyaniline in the base form dissolved in 100% solvent N-methylpyrrolidinone (NMP). The vertical axis is the ultraviolet visible (UV VIS) detector response and the horizontal axis is the peak retention time in minutes. Two peaks are evident in Fig. 1, peak 2 which corresponds to a weight average molecular weight of approximately 371,700 and peak 4 which corresponds to a weight average molecular weight of approximately 29,500. Fig. 2 shows the GPC of polyaniline in the base form in NMP/.5 wt % lithium chloride (LiCl) which shows a single peak 6 corresponding to a weight average molecular weight of approximately 45,500. It is evident in comparing Fig. 1 to Fig. 2 that the high molecular weight peak 2 of Fig. 1 has disappeared and that the molecular weight of ì the major peak is higher than that in NMP, corresponding to a higher hydrodynamic volume. Fig. 5 is a plot of a first run of a dynamic mechanical thermal analysis (DMTA) plot of an undoped polyaniline base film cast from 100% NMP. The as-cast film contains approximately 21%ìè NMP which is determined from thermo gravimmetric analysis. The dashed line in Fig. 5 which is the plot of tan(δ) shows several transitions of which some are related to the residual solvent. Fig. 6 shows a plot of a DMTA (second run) of the same material as for Fig. 5. The solvent is substantially driven off in the first run. The single peak of the dashed curve which corresponds to the tan (b) measurement shows that the polyaniline base has a glass transition temperature ( T g ) of 251°C. Fig. 7 shows a plot of a DMTA (second run) for polyaniline base, cast from 100 wt% NMP, which has been doped in 1N HCl and subsequently undoped with .1M NH 4 OH. Most of the NMP was removed in the process. It has been determined from thermogravimmetric analysis (TGA) that there is only 2.8% NMP remaining in the film. The glass transition temperature of this sample is 256 ì degree C, relatively the same as that measured for the sample of Fig. 6. Fig. 8 shows a plot of a DMTA (second run) of polyaniline base cast from 99.5 wt% NMP/.5 wt% lithium chloride. The peak in the tan(δ) curve gives a T g of 180"C. Table I summarizes the results of Figs. 5-8 and also gives additional results for films cast from combinations of NMP and m-cresol and a surfactant nonylphenol. Material History Tg from DMTA (°C) Polyaniline Base Cast from 100%NMP Thermally annealed* (0% residual NMP in film) 251 Polyaniline Base cast from 100% NMP Doped with HCL undoped in ammonia (2.8% residual NMP in film) 256 Polyanilinc Base cast from 90 wt % NMP/10 wt % m-cresol Thermally annealed 186 Polyaniline Base cast from 75 wt % NMP/25 wt % m-cresol Thermally annealed 175 Polyaniline Base cast from 99.5 wt % NMP/0.5 wt % LiCL Thermally annealed 180°C Polyaniline Base cast from 99 wt % NMP/1 wt % nonylphenol Thermally annealed 222°C The drop in glass transition temperature of the polyaniline base upon exposure to an additive such as m-cresol, LiCl and nonylphenol indicates that there is a drop in the crosslink density of the polyaniline base material as a result of deaggregation of the polyaniline base molecules. While applicant's do not want to be limited to a particular theory, this cross-link is believed to be in the form of inter-chain or intermolecular hydrogen bonding. Fig. 9 shows two polyaniline base molecules wherein a hydrogen atom from an amine site on one molecule is hydrogen bonded as represented by the dashed line to an imine nitrogen on an adjacent molecule. Fig. 10 shows the effect of adding lithium chloride to the arrangement shown in Fig. 9. The lithium chloride can complex with the imine nitrogen lone pairs as shown in the Fig. 10 thereby disrupting the interchain hydrogen bonding between polyaniline chains. Fig. 11 is a schematic diagram showing three polyaniline molecules 20, 22 and 24 wherein there are a plurality of hydrogen bonds 26 interlocking each of the three polyaniline molecules shown. It is evident from Fig. 11 that where there is a high density of hydrogen bonding between adjacent polyaniline molecules, there is effective crosslinking between the molecules which will affect the glass transition temperature of a polyaniline material. (Generally the glass transition temperature increases as the cross-linking density increases.) The high degree of crosslink density will result in a significant degree of aggregation of polyaniline molecules. The atomic force micrograph (AFM)(Fig. 15) of the polyaniline film processed from 100% NMP shows "clusters" or "bundles" on the order of 100 nm. This structure agrees well with previous results on evaporated films (no solvent) by T.L. Porter et al., Surface Science, 293, 81 (1993). When the hydrogen bonded and ravelled molecules of Fig. 11 are exposed to a deaggregating agent such as LiCl, an inter-molecular structural change occurs wherein the molecules are no longer hydrogen bonded and the molecules are unravelled and deaggregated. The present results together with the previous results by Porter indicate that polyaniline in the solid-state is highly aggregated. (Examples of solid state forms of polymers are powders and films.) When the polyaniline is then dissolved in NMP, the NMP does not appreciably solvate the polyaniline to disrupt the interchain interactions of the polyaniline and the material remains aggregated. When the polyaniline molecules are exposed to a dopant, this high degree of aggregation will prevent the dopant from being able to dope all regions of the polyaniline molecules uniformly and may be responsible for the formation of the metallic islands characteristic of conducting polyaniline (described above) which are approximately 20-30 nm (200-300 &angstrom). This will result in less than an optimal conductivity for a doped polyaniline material. If the aggregated polyaniline molecules are deaggregated by the methods according to the present invention, the polyaniline molecules will be more effectively doped when contacted with a dopant. In this fashion the size of the metallic islands may in turn be increased above 20-30 nm (200-300 &angstrom) thereby enhancing the mobility of the carriers, and in turn the electrical conductivity. It may be possible to ultimately eliminate the formation of islands by more uniform doping; in this fashion the material would be more homogeneous and hopping through less conducting regions to go from metallic island to metallic island would thereby be eliminated. An exemplary list of solvents useful to practice the present invention is: List of Solvents: N-methyl pyrrolidinone (NMP) dimethyl sulfoxide (DMSO) dimethyl formamide (DMF) pyridine toluene xylene m-cresol phenol dimethylacetamide tetramethylurea n-cyclohexylpyrrolidinone aqueous acetic acid aqueous formic acid pyrrolidinone N 1 N' dimethyl propylene urea (DMPU) benzyl alcohol water An exemplary list of salts which can be used as a deaggregation ì agent or additive is: Salts: lithium chloride lithium bromide lithium iodide lithium fluoride lithium tetrafluoroborate lithium hexafluorophosphate lithium perchlorate lithium phenoxide lithium triflate lithium niobate magnesium bromide magnesium chloride magnesium ethoxide magnesium fluoride magnesium sulfate magnesium perchlorate magnesium nitrate sodium bromide sodium chloride sodium chlorate sodium hexafluorophosphate potassium bromide potassium chlorate potassium chlorideìè potassium fluoride potassium hexafluorophosphate rubidium chloride rubidium fluoride rubidium nitrate cesium bromide cesium chloride cesium floride cesium iodide calcium bromide calcium chloride calcium iodide calcium nitrate barium chloride barium fluoride barium iodide barium sulfate barium perchlorate tetrabutylammonium chloride tetrabutylammonium fluoride tetrabutylammonium hexafluorophosphate tetrabutylammonium iodide tetrabutylammonium nitrate tetraethylammonium iodide, etc. tetramethylammonium bromide, etc. tetrapentylammonium bromide, etc. An exemplary list of surfactants which can be used as a deaggregation agent or additive is: Surfactants: Reference: Encyclopedia of Chemical Technology, 3rd Edition, K. Othmer, Wiley-Interscience, Pub., vol. 22, p. 332 (2) nonionic surfactants - Examples i) polyoxyethylene surfactants (ethoxylates) namely - alkylphenol ethoxylates RC 6 H 4 ( OC 2 Hì sub 4) n OH e.g., Triton N-57 Triton N-111 Triton X-45 Triton X-102 Triton X-305 Triton X-705ìè ii) alkylphenols, e.g. nonylphenol, docecylphenol An exemplary list of dopants which can be used to dope the polymer to the conducting state are: hydrochloric acid, acetic acid, formic acid, oxalic acid, toluenesulfonic acid, benzenesulfonic acid, naphthalene sulfonic acid and, methyliodide. When deaggregation is done in solution the deaggregating agent is present in an amount less than about 25 wt%. When deaggregation is done in solution using a salt as the deaggregation agent, the salt is preferably present in an amount from about 0.00001 wt% to about 5 wt%, more preferably from about 0.0001 wt% to about 2.5 wt%; most preferably from about 0.001 wt% to about 1 wt%. When the deaggregation is done in solution using a surfactant as the deaggregation agent, the surfactant is preferably present in an amount from about 0.0001 wt% to about 10 wt%; more preferably from about 0.001 wt% to about 5 wt%; most preferably from about 0.01 wt% to about 2.5 wt%. When the deaggregation is done in solution using an acidic additive as the deaggregation agent, the acidic additive is preferably present in an amount from about 0.0001 wt% to about 25 wt%; preferably from about 0.001 wt% to about 15 wt%; most preferably from about 0.01 wt% to about 10 wt%. Fig. 15, 16, 17, 18, 19 and 20 are atomic force micrographs each having a dimension of 1000 nm X 1000 nm. Fig. 15 is for polyaniline base cast from 100% NMP; Fig. 16 is for polyaniline cast from 100% NMP and subsequently exposed to m-cresol; and Fig. 17 of the same sample as in Fig. 16 with the m-cresol pumped out and shows no tendency to re-aggregate. Fig. 15 shows aggregated ì regionsìè of the order of 100 nm. Fig. 16 shows the substantial elimination of the aggregated regions caused by exposure to the deaggregating agent, m-cresol, which remains when the m-cresol is removed. Therefore, the deaggregated structure is locked or remains without the deaggregating agent. Fig. 15 shows bundles of aggregated regions which are not present in Fig. 16 and 17. Figs. 18, 19 and 20 show similar results for treatment with nonylphenol and triton surfactant. The level of deaggregation is not as complete as in Fig. 16 but shows the onset of deaggregation. Basic Synthesis of Polyaniline Unsubstituted Polyaniline The unsubstituted polyaniline is synthesized by the chemical oxidative polymerization of aniline in 1N HCL using ammonium peroxydisulfate as an oxidizer. Polyaniline can also be oxidatively polymerized electrochemically as taught by W.Huang, B. Humphrey, and A.G. Macdiarmid, J. Chem. Soc., Faraday Trans. 1, 82, 2385, 1986. In the chamicl synthesis, the conducting polyaniline:hydrochloride salt precipitates from solution. The polymerization is allowed to proceed for several hours after which the powder is filtered, washed with excess 1N hydrochloric acid. The polyaniline:hydrochloride is then converted to the nonconducting or non-doped polyaniline base by reaction with 0.1M ammonium hydroxide. The polyaniline base is then filtered, washed with ammonium hydroxide, then washed with methanol and dried. The polymer in this stage is in the undoped base form as a powder. The polymer is generally processed by taking the polyaniline base powder and dissolving it in organic solvents, most commonly N-methylpyrrolidinone. This solution can be used to spin-coat thin films of the base polymer or can be used to solution cast thick films or can be used to fabricate structural parts of the polyaniline base. The substituted polyaniline derivatives are made by the oxidative polymerization of the appropriate substituted aniline monomer. Copolymers can also be made by the oxidative polymerization of one or more monomers. In addition different acids other than hydrochloric acid can be used in the synthesis. Doping generally involves reaction with most commonly protonic acids. Other electrophiles can also be used as dopants, for example alkylating agents, etc. The doping can be done in solution or it can be done heterogeneously in the solid state. For example, the NMP solution of the polyaniline base can be used to spin-coat films of the polyaniline base. These films can be doped or made conducting by dipping into a solution of the appropriate acid such as 1N HCL, or aqueous toluene sulfonic acid or the vapor of the acid. The polyaniline base powder can also be doped by stirring in an aqueous solution of the dopant. The doping can also be carried out in solution which is generally preferred as it allows the conducting form to be processable. To the NMP solution of the polyaniline base is added the appropriate dopant, for example camphorsulfonic acid. The acid reacts with the polyaniline base to form the conducting polyaniline salt. Any ì other acid or electrophile can be used in the same manner. The conducting salt will either precipitate or remain in solution depending on the particular dopant used. If it stays in solution, the conducting solution can then be used to fabricate films of the conducting polyaniline by spin-coating, dip coating, spray-coating, etc. or fabricated into some structural components. Typical experimental for the additives: The present invention uses additives in the starting solvent, eg. NMP. For example, 0.00001 wt % to 5 wt %, preferably 0.0001 to 2.5 %, and most preferably .001 to 1% ratio) LiCl is added to the NMP. The salt is allowed to dissolve in the NMP. To this solvent is added the polyaniline base powder and allowed to stir. Once the polyaniline base is dissolved, it is filtered through a 0.2 micron millipore filter and then to the filtered solution is added the dopant. Dopants used in this study include toluenesulfonic acid, camphor sulfonic acid, acrylamidopropanesulfonic acid, hydrochloric acid. The conductivity of the polyaniline salt is found to depend on the processing conditions. Generally polyaniline doped heterogeneously with aqueous 1N HCL gives conductivity on the order of approx. 1 S/cm. Doping in NMP generally gives much lower conductivity (approx. .1 S/cm). A great deal of variation in conductivity has been observed depending on the solvent system used for doping. When a polyaniline base is doped in NMP with an organic sulfonic acid a localized polaron peak is observed on the ultraviolet-visible near IR spectrum. When this film is exposed to m-cresolìè a highly delocalized polaron peak is observed extending out to 2500 nm with the conductivity increasing to hundreds of S/cm. Conductivity of .2 S/cm is attained when an NMP solution of the polyaniline base is reacted with camphorsulfonic acid or acrylamidopropanesulfonic acid. The uv/visible/near IR spectrum for the polyaniline doped with acrylamidopropane sufonic acid is shown in Fig. 12. As can be seen a localized polaron peak 10 is attained. When .5 wt.% LiCl is added to the NMP, a delocalized polaron peak 12 (Fig. 13) is attained and with 1 wt. % LiCl a highly delocalized polaron peak is attained (Fig. 14). This delocalized polaron is indicative of higher conductivity as a result of more highly delocalized carriers. Also, an NNP/additive (e.g. LiCl) solvent system was used to spin-coat the polyaniline base films. The UV of the base also shows a red shift to longer wavelengths with the incorporation of additives as compared to films cast from 100% NMP. This red shift is indicative of an extension of the conjugation length. When these films are doped with hydrochloric acid vapor, the films which include the lithium chloride show a more highly delocalized polaron peak as compared to the NMP film alone. The additives can also be surfactants such as nonylphenol or the tritons. The triton for example is dissolved in the NMP prior to the addition of the pani base as described above. This solution was used to cast thick films of the pani base. Upon doping of the thick films with hydrochloric acid, the conductivity of the film was 11 S/cm for the triton containing film; 40 S/cm for the nonylphenol containing film; and only 1 S/cm for the NMP only film. Films processed according to the present invention can give rise to enhanced stretch orientation and a corresponding increase in electrical conductivity. Fig. 21 schematically shows an undoped deaggregated film 20 held at end 22 and end 24 by clamps 26 and 28 respectively. Ends 22 and 24 are pulled apart as indicated by arrows 30 and 32, respectively. The molecules in the deaggregated film are unravelled and therefore when film 20 is stretched there is increased propensity for alignment of the molecules in the stretch direction and thereby enhanced electrical conductivity in the stretch direction. Solutions processed according to the present invention exhibit enhanced shelf life stability. Polyaniline solutions in general tend to gel over time. The time for gelling to occur is dependent on solvent and concentration of solids in solution. For example, a solution of polyaniline base in NMP made to 5% solids be weight tends to gel within days. Solutions higher in solids content gel within minutes. Gellation limits the full use of the polyaniline solutions for many applications. Gellation occurs because of interactions between chains, most probably hydrogen bonding. As the hydrogen bonding between chains increase, chain entanglements increase. As this entangled or highly aggregated structure is less soluble than the non-aggregated structure, the solutions of the aggregated structure in turn gel. The addition of salts such as lithium chloride, for example, breaks the interchain hydrogen bonds and in turn prevents the solution from gelling thereby enhancing the long term shelf life stability of the polyaniline solutions. Also, the use of these additives allows higher solids polyaniline solutions to be made (higher than can normally be made without the additives) with good shelf life stability.

Claims: A cast film of matter comprising: an electrically conductive polymer selected from the group consisting of electrically conductive substituted and unsubstituted doped polyanilines, whereby said dopant is selected from the group consisting of hydrochloric acid, acetic acid, formic acid, oxalic acid, toluenesulfonic acid, benzenesulfonic acid, naphthalenesulfonic acid and methyliodide, said composition additionally comprising a deaggregating agent, said desaggregation agent being selected from the group consisting of alkylphenol- and alkylphenol-ethoxylate surfactants and a salt, wherein said salt is selected from the group consisting of lithium salts, magnesium salts, sodium salts, potassium salts, rubidium salts, cesium salts, calcium salts, barium salts, tetrabutyl ammonium salts, tetraethyl ammonium salts, tetramethyl ammonium salts and tetrapentyl ammonium salts. A film according to claim 1, wherein siad electrically conductive polymer includes aggregated regions that are smaller than those aggregated regions present in said electrically conductive polymers not comprising said deaggregating agent. A film according to claim 1 or 2, wherein said polymer moelcules have a glass transition temperature less than the glass transition temperature of said polymer molecules without said deaggregating agent. A film according to any one of claims 1 to 3, wherein said polymer molecules have a deaggregated structure. A film according to any one of the preceding claims, wherein said polymer molecules have an expanded coil conformation. Method for forming a cast film of matter according to any one of claims 1 to 5, characterized by the steps of doping the polyaniline polymer; and treating said doped polyaniline polymer with said deaggregating agent.

Inventors: ANGELOPOULOS MARIE, FURMAN BRUCE K, ANGELOPOULOS, MARIE, FURMAN, BRUCE K.
Applicants: IBM, INTERNATIONAL BUSINESS MACHINES CORPORATION
Application year: 1995
Main classification: H01B1
IPC codes: H01B1