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In this study, we synthesized the new kinds of semiconducting polymeric gels having negative (n-type) and positive (p-type) counter ions as charge carriers. The polyacrylamide gel was doped with pyranine (8-hydroxypyrene-1,3,6-trisulfonic acid, trisodium salt), havingions as side groups and Na+ as counter ions, so-called p-type semiconducting gel. The doping process was performed during the polymerization where the pyranine binds to the polymer strands over OH group chemically via radical addition. In a similar way, N-isopropylacrylamide (NIPA) gel was doped with methacrylamidopropyltrimethyl ammonium chloride (MAPTAC), having Cl− as counter ions, so-called n-type semiconducting gel. Here MAPTAC was embedded by copolymerization within the polymer network (NIPA). These semiconducting gels can show different electrical properties by changing the concentration of the doping agents, swelling ratio etc. We have shown that the pn junction, formed by combining p-type and n-type gels together in close contact, rectifies the current similar to the conventional Si and Ge diodes.
The discovery of the silicon pn junction is a landmark in the development of modern microelectronics. Silicon and other inorganic semiconductors are the predominant materials in electronic manufacturing today; however, the development of organic-based electronic components has been a focus of intensive research and development. Organic electronics have become an active research area in recent years because they are an alternative to the traditional semiconductor technology and challenges in design on a smaller scale from microscale to nanoscale. Moreover, organic materials have vast potential for integration in low-cost microelectronic devices. Organic-based semiconductors, for example polymeric gels, may have superior properties due to their flexibility against to regulate some physical properties of the materials even after the production, e.g., by changing the volume of the gel. Circuits and displays based on organic electronics may also be flexible, low-weight, and environment friendly. Due to great diversity and functionality of the polymers, they may also be produced for specific requirements, like biocompatible semiconductors. Last, some water-tolerant organic devices may be biocompatible, that is, they may be used in circuits that directly reside on or are implanted inside animal and human tissue and could perform various sensing, interfacing, and controlling functions for drug delivery, prosthetics, and neural-electronic integration.
Insulating polymers have been made conductive so far by using various methods such as ion implantation [1-4], press contacting [5,6], and photochemical doping . The impressive properties of these materials that have been taken advantage are the ability to manipulate electronic properties by changing their molecular structure . Differently current rectifying in semiconductor diodes via diffusion of ionic charges across a pn junction sets up a built in potential; there is unidirectional current is observed across a membrane where a built in potential arises from diffusion of anions and cations in organic junctions .
We considered that the principle of the electrical conductivity in polymeric gels can be changed by doping static (inactive) ions having counter ions as charge carriers and these gels can be used to form pn junctions that work similar to inorganic semiconductors. These semiconductor polymeric gels can be doped with both negative (n-type) and positive (p-type) counter ions as charge carriers. We have shown that the pn junction formed by combining p-type and n-type gels together in much closer contact rectifies the current.
p-type hydrogels were synthesized via free radical cross-linking co-polymerization of acrylamide (AAm) and N,N′-methylene bisacrylamide (BIS) as crosslink agent in the presence of pyranine (8-hydroxypyrene-1,3,6-trisulfonic acid, trisodium salt) in varying amount, 10−6, 10−4, 10−2 mol/l [10-12]. Ammonium persulfate (APS) was used as the initiator. The ratios of AAm to BIS and AAm to APS were kept fixed for all samples; AAm/BIS = 31 and AAm/APS = 43 in bidistilled water. The samples were deoxygenated by bubbling nitrogen during 10 min, and the gelation was performed in the 1 × 1 cm2 square-shaped holders (4 cm3 of volume) at 60°C in a heat bath.
After gelation processes were completed, gels were washed with pure water during 15 days with changing their water every day. Thus, pollutions and unreacted chemicals washed out from the gel, and only pyranines, which were bound to the polymer strands chemically [10-12], were stayed in the gel. After the gels dried at 40°C furnace, they were cut into thin slices with ~1 mm thickness for electrical measurements.
n-type gels were synthesized, similar to p-type, as free radical cross-linking co-polymerization of N-isopropylacrylamide (NIPA) and N,N′-methylene bisacrylamide (BIS) as crosslink agent in the presence of methacrylamidopropyltrimethylammonium chloride (MAPTAC) in varying amount, 3 × 10−6, 3 × 10−4, 3 × 10−2 mol/l [13-15]. 2,2- Azobisizobütilonitril (AIBN) was used as an initiator. The ratios of NIPA to BIS and NIPA to AIBN were kept fixed for all samples; NIPA/BIS = 50 and NIPA/AIBN = 71 in Dimethylsulphoxide (DMSO). These gels were prepared for electrical measurements in similar way with p-type gels.
AAm, NIPA, and doping concentrations of the samples were summarized in Table Table11.
To be able to evaluate the net effect of the doping on the electrical properties, samples p1, p5, n1, and n5 were synthesized without doping agents for comparison with the other samples.
Electrical measurements were taken on Keithley, Model 6487 Picoammeter/Voltage Source. The gels, prepared in the slice shapes of area A and thickness D, were swollen to a certain swelling ratio, and then placed between platinum electrodes, and sealed from the air against drying. The current densities per unit mass, J/m, of the gel were measured against the time, the applied voltage and the swelling ratio of the gels. The detailed discussions about these measurements are given in results and discussion part.
The pyranine binds to the polymer chains, over its OH group, chemically during the polymerization as it is discussed in detail in references [10-12], and they form stable charged sites doped with positive counter ions. Thus, the polyacrylamide gel is doped with pyranine having ions as side groups and Na+ as counter ions, so-called p-type semiconducting gel .
Similarly, NIPA gel was doped with MAPTAC, having Cl− as counter ions, so-called n-type semiconducting gel. The MAPTAC binds to the polymer chains chemically during the polymerization, thus they form stable charged sites doped with negative counter ions as represented in Scheme Scheme1together1together with the p-type gel. This doping process was also discussed in detail in references, [10,14,15]. When these gels are in the collapsed state, no current is observed. When the gels start to swell, the current starts to flow through the gels.
The currents decrease with time for a constant applied voltage as shown in Fig. Fig.1a1a for p1, p2, p3, and p4 samples. This decrease in the currents is a direct indication of the ionic conductivity. As the charge carriers (the ions in water phase of the gel) were gathered on the electrodes, the density of the charge carriers decrease in time, and thus the current. As seen, the initial values of the currents measured for the doped gels are considerably bigger than that of the “neat” gel (the gel that was not doped with ions) at a certain swelling ratio, V/V0 = 1.28 and under constant applied voltage, U = 5 V. Furthermore, the initial amplitude of the currents increases with increasing doping concentration. This clearly shows that the net charge in the gel increases with increasing doping concentration.
Examples for the short-cut experiments -the source of the voltage was removed and the current was measured by means of an ammeter without changing its polarity- were also indicated in (Fig. (Fig.1b)1b) where all the current takes first a negative value, as it is expected, and then goes to zero with time.
Figure Figure11 clearly indicates that the free charges leading the current are accumulated on the surfaces of the gel on which the voltage is applied (similar to charging a parallel plate capacitor) and the gels have ionic charge carriers.
Figure Figure2a2a shows typical current-time plots of the slab gels for increasing pyranine content. The gels were swollen in pure water up to certain swelling degree (V/V0 = 1,3), under a fixed applied voltage, 1 V. As seen, the currents for all samples decrease with time; however, the initial values of them increase with increasing doping agent (pyranine content).
Figure Figure2b2b shows the ratio of the normalized current densities (J/mgel) for doped (p8) to neat (p5) gels as function of the applied voltage for varying swelling ratio. The currents were measured 5 s later just after applying voltage. As seen, the doping effect on the current decreases when the swelling ratio is increased. This may be due to the vast increase in the free ions coming from the water which causes screening. This picture may indicate that doping effect (p-type behavior) can be fulfilled up to a certain swelling degree of the above-mentioned gel which semiconducting behavior will be lost.
The instantaneous currents—the currents that were measured 5 s later just after changing the voltage- as function of the volume of the gels for varying voltages were also measured, and the results were indicated in Fig. Fig.3.3. As seen from this figure, distinct peaks appear as the solvent uptake, V/V0, increases. The peaks almost disappear for the gels doped with pyranine due to increasing homogeneity of the gels in the presence of the ions . The results coincide with the recent literature where three dominant peaks, each corresponding to a different swelling stage in the conductivity, were observed . Figure Figure33 indicates that the volume of the gel is one of the main parameters determining the current.
These peaks were related to the distribution of dense polymer regions; they are defined as the “blobs” appearing in a microstructure of the given PAAm gel having at least some average sizes. This special behavior in these gels may result specific features related to the electrical features. The heterogeneity of the gel may decrease essentially in case when it is prepared with the charged groups. The internal electric field due to the charged sites could disturb the tendency between the polymer units (affinity of the AAm momoners to the cross-linker molecules) because the charge excess has a tendency to form denser polymer regions especially in mesoscale regions. The formation of the rigid network in the charged gel makes it more homogenous in comparison with the neutral gel. This could cause the decreasing amplitude of the peaks, and overall decrease in the conductivity as it is confirmed by Fig. Fig.33 (see also Fig. Fig.22 of reference ). Therefore, in the charged gel, the penetration of neutral water molecules through the system of large channels located in the vicinity of small blobs is facilitated. Because of this fact the total value of the dc conductivity is decreased.
Figure Figure44 represents the normalized current density per unit mass as function of the voltage for the gels (sample p3) swollen with water (Fig. (Fig.4a)4a) and DMSO (Fig. (Fig.4b).4b). DMSO is not a polar molecule; therefore, the ions like H or OH are absent in it. As seen from this figure, the current density decreases fairly for the gels swollen with DMSO since no contribution to the current occurs via H and OH ions. The current occurs mainly due to doped ions (the counter ions of the doping agent). This observation clearly indicates that the possible negative effects of the water upon the pnjunctions that may be formed by means of our gels can be eliminated.
All the above-mentioned measurements were repeated for n-type gels, and the similar results were reproduced. Here the results are not given to avoid the repetition.
In Fig. Fig.5,5, representative examples of I-U(current–voltage) character of polymeric diode are given for the neat and the doped gels. Figure Figure5a5a shows the current–voltage character that was made by means of close connection of p-(sample p4) and n-type (sample n4) slab gels- putting one of the gel on the top of the other for each gel. The swelling ratio of each gel was kept the same, V/V0 = 1,2. When the neat gels are used for both the p-and n-type sides, no rectification is observed as can be seen from Fig. Fig.5b.5b. Figure Figure5a5a clearly shows that the current of the interface between the cationic and anionic gels, which is passing through only one direction, originates directly from the doping effect of the gels.
In this study, we have shown that p- and n-type doped hydrogels can be synthesized and be used to built pn junction. The synthesis of these gels and making junctions are more simple, inexpensive, and scalable than traditional pn junctions. Moreover, they could be used in flexible and biocompatible electronic circuits. The current–voltage characteristic of the polymeric pn junction can be changed by changing doping concentration, swelling ratio etc that will be discussed in our feature works.
The percentage of the standard deviations changes around 20% as can be seen from Fig. Fig.1a.1a. The reasons for this high standard deviations can be explained by the following arguments: (1) The electrical futures of these gels depend strictly on the swelling ratio of the gels as can be seen from Fig. Fig.33 and from the detailed discussion given in a recent work  and (2) on the internal morphology (nonergodicity or random distribution of the heterogeneous regions in the gels). This strict volume dependence and the randomness of the internal distributions of the heterogeneous regions [18,19] set a barrier for comparison of the samples from the point of the current amplitudes due to the difficulties to bring the gels to exactly the same swelling ratios and to repeat the synthesis with exactly the same internal morphology. Therefore, the stability and reversibility problems need detailed experiments and probably more controllable polymer synthesis.
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