Wednesday, December 17, 2014

Growth of 2-inch size Ce:doped Lu2Gd1Al2Ga3O12 single crystal by the Czochralski method and their scintillation properties


Pr: (Lu,Y,Gd)3(Ga,Al)5O12 single crystals were grown by the m-PD method.
The grown LGAGG showed light yield of around 25,000 photons/MeV and energy resolution was 9.8%@662 keV.
The scintillation decay time was 53.6 ns at room temperature.
The density of LGAGG is theoretically 7.13 g/cm3.

Ce 1% doped Lu2Gd1Al2Ga3O12 (LGAGG) single crystals with a diameter of 50 mm and length of 150 mm were grown by the Czochralski (Cz) method using an RF heating system. The EPMA techniques is employed to check homogeniousity of chemical composition. Luminescence and scintillation properties were also evaluated. The grown LGAGG showed light yield of around 25,000 photon/MeV and energy resolution was 9.8%@662 keV. The scintillation decay time was 53.6 ns at room temperature.


Tuesday, December 2, 2014

Measurement of the temperature coefficient of Young's modulus of single crystal silicon and 3C silicon carbide below 273 K using micro-cantilevers

    • Highlights

      Measurement of the temperature coefficient of Young's modulus of Si in the temperature range of 200–290 K.
      Measurement of the coefficient of SiC in the range of 210–295 K.
      Temperature coefficient of Young's modulus of silicon: −52.6 ± 3.45 ppm/K.
      Temperature coefficient of Young's modulus of silicon carbide: −39.8 ± 5.99 ppm/K.


      This paper reports on the measurement of the thermal coefficient of Young's modulus of both single crystal silicon and 3C silicon carbide over the temperature range spanning 200–290 K. The thermal coefficients were determined by monitoring the change of resonance frequency of micro-cantilevers as their temperature was reduced. The thermal coefficient of Young's modulus, 1/E · δE/δT was measured to be −52.6 ± 3.45 ppm/K for silicon and −39.8 ± 5.99 ppm/K for 3C silicon carbide, agreeing well with theoretical predictions, and also with experimental values that have been previously published for temperatures above 273 K. This work has therefore expanded the temperature range over which the thermal coefficient of Young's modulus has been measured to below 273 K and towards the temperatures required for low-temperature military and space applications.


      Single crystal silicon carbide;
    • Young's modulus
    • Low temperature
    • MEMS cantilever
    • Laser vibrometry
    • Silicon carbide

  • Soure:Sciencedirect

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Wednesday, September 17, 2014

Structural and Third-order Nonlinear Optical Properties of Lithium Hydrogen Phthalate Dihydrate Single Crystals

Single crystals of Lithium Hydrogen phthalate dihydrate (LHP), a semi-organic nonlinear optical material have been successfully grown from aqueous solution, by slow evaporation solution growth technique. Single crystals in size 40×10× 5 mm3 were grown in a period of 2 weeks. The grown crystals were characterized by single crystal X-ray diffraction. LHP crystallizes in Pnm space group of Orthorhombic system, with the unit-cell dimensions at 293(2) K; a = 16.8356(10) Å; b = 6.8187(5) Å; c = 8.1967(6) Å; α = 90°, β = 90°, γ = 90°. Third order non-liner studies have also been studied by Z-scan techniques. Nonlinear absorption and nonlinear refractive index were found out and the third order bulk susceptibility of compound was also estimated.

1. Introduction: 
The semi-organic alkali hydrogen phthalate crystals are widely known for their application in the long-wave Xray spectrometers (A G. Boehm and K. Ulmer, 1971). Their optical, piezoelectric, NLO and elastic properties are 
investigated in detail (N. Kejalakshmy, K. Srinivasan 2004; S. Haussühl 1991; Andrzej Miniewicz, and Stanislaw 
Bartkiewicz 1993). Acid phthalate crystals were used as substrates for deposition of thin films of organic nonlinear 
materials (W. Sander et al. 2007) and standards in volumetric analysis (Sterling B. Smith 1931). 

Lithium Acid Phthalate possesses piezo-electric, pyro-electric, elastic and non-linear optical properties  (H. 
Kuppers, et al.1985; A.Senthil, et al. 2009; Shankar, M. V. and Varma, K. B. R. 1996). These crystals have excellent physical properties and have a good record for long term stability in devices (E.W. Vanstryland, et al. 1998). Tuning of band gap in semiconductor materials is an important tool in optoelectronic and photonic integration. The optical behavior of materials is an essential parameter to determine its usage in optoelectronic devices (Shahabuddin Khan M. D. and Narasimhamurty T. S., 1982. In the present work, single crystal of Lithium hydrogen phthalate dihydrate (LHP; also known as lithium acid phthalate), a semi-organic NLO, has been grown by slow evaporation technique. Though the Second order NLO property of LHP crystals was already reported, its Third Order NLO property has not been reported yet. The grown crystals were subjected to single-crystal X-ray diffraction, Fourier transform infrared (FTIR) analysis and thermal. In addition, third order NLO property of the LHP crystal was confirmed by the Z-scan studies. Also, here we reported the theoretical calculation for the determination of the nonlinear refractive index, in order to tune these factors for the requirements of the device and the results are discussed details.  

2. Experimental procedure:
Lithium hydrogen phthalate  dihydrate (LHP.2H2O) was synthesized with high purity Lithium hydroxide 
(98% E-Merck) and phthalic acid (98% E-Merck) GR grade in the ratio1:1. The stoichiometric amounts of the 
reactants were dissolved in the de-ionized water and stirred well for about 4 hours (Temperature approximately at 
55°c).This was then filtered and allowed to crystallize by slow evaporation technique (G. Adiwidjaja and H. Kupper 
1978).  The seed crystals with transparency were obtained by spontaneous nucleation. Among them, defect free seed crystal was suspended in the mother solution which was saturated at 34°C in constant temperature bath of ±0.05K accuracy. Optically good bulk crystals have dimension (4.5×1.0×0.7) cm has been grown within the period of 25 days and shown in Fig 1. 

3. Results and discussion:
3.1 Single crystal X-ray diffraction analysis:  Three-dimensional intensity data of a transparent and good quality crystal were collected on an Enraf-Nonius CAD-4 diffractometer equipped with MoKα radiation  λ=0.71073Å. ω/2θ scan mode was employed for data collection. LHP crystallizes in an orthorhombic crystal system with the unit-cell dimensions at 293(2) K;  a = 16.8356(10) Å; b = 6.8187(5) Å ; c = 8.1967(6) Å ; α = 90°, β = 90°, γ = 90°.

3.2 Microhardness measurements: 
From application point of view, hardness is an important solid state property of the single crystals as it 
plays a vital role in device fabrication. Hence Vicker’s Microhardness measurement was carried out for Lithium 
Hydrogen Phthalate crystals to assess their mechanical strength. To evaluate the vicker’s hardness number, as grown crystals of LHP was subjected to static indentation test at room temperature using Leitz wetzlar hardness tester fitted with vicker’s diamond pyramidal indentor. Several indentations were made on the (0 0 1) face of LHP single crystals. The vicker’s hardness number was calculated using the expression;
Fig 2. Microhardness Vs Load for LHP single crystals Surface pattern of indented area for 100 gram load along (0 0 1) plane of LHP, Crystals where Hv is the vicker’s hardress number for a given load, P in gram and d is the average diagonal length of the indentation in mm. For loads ranging from 25 - 100 gram, the micro-hardness values of  LHP  was found to be in the increasing trend and it could be seen through Fig 2. When the indenter just touches the surface of the crystal, a dislocation is generated in the indenter region and thus causes the increases of Microhardness of the compounds initially. However, for the loads beyond 100 gram, cracks started developing around the indentation mark. The Hardness (HV) then decreases with load and saturates for higher loads which occur due to the rearrangement of dislocations and mutual interactions of dislocations.

3.3 Dielectric measurements
Dielectric studies have been performed on (010) planes of  lithium hydrogen phthalate single crystals at 30º 
C, 50º C and 75º C in the frequency range 50Hz – 5MHz using (LCR HIOKI-3532 LCR HITESTER) LCR meter. 
The sample has been coated with conductive silver paint for metallic contacts. A sinusoidal a.c. voltage was applied to the sample through the silver electrodes for various frequencies. Capacitance developed by the crystal was recorded and the dielectric constant has been calculated using the area and thickness of the sample.  

The dielectric constant decreases with increase in frequency and after reaching a frequency of 1 MHz, the 
dielectric constant almost remains a constant Fig.3.  The total dielectric polarization of materials is from the 
contribution of electronic, ionic, dipolar and space charge polarizations at lower frequencies and the value of εr
rises predominantly due to orientation of dipoles in the low frequency of range 1kHz  –  5MHz. Since, the orientation polarization is highly dependent on temperature; the change in temperature of samples marginally affects the value of εr.Dielectric loss calculated at various frequencies reveals that the power loss of the sample on applying electrical energy was found to be negligible. 

3.4 UV-Vis-NIR 
UV-Vis-NIR measurement was carried out for Lithium hydrogen phthalate dehydrate single crystals in the 
wavelength range 200-1200nm using a Varian Cary 5E UV and shown in Fig 4.

The maximum UV absorption occurs at 205nm. After this wavelength, absorption abruptly decreases to 
nearly 1.5-4%. The material possesses a very good optical transparency even up to 1500nm. This property would be much useful in field of an optical material.

3.5 Z-scan Measurement
The Z-scan method has gained rapid acceptance by the nonlinear optics community as a standard technique 
for separately determining the nonlinear changes in refractive index and the change in nonlinear optical absorption. The nonlinear absorption and refractive index of LHP crystals (thickness ≈0.945x10
-3 m) were estimated using the single beam Z-scan method with laser beam intensity of 60mW and the wavelength of source used for the 
measurement was 632.8 nm. The study of nonlinear refraction by the Z-scan method depends on the position (Z) of 
the thin samples under the investigation along a focused Gaussian laser beam. The sample causes an additional 
focusing or defocusing, depending on whether nonlinear refraction is positive or negative. Such a scheme, referred 
to as an “Open aperture” Z-scan and it is suited for measuring nonlinear absorption in the sample. Results obtained 
from a typical closed aperture Z-scan study for the grown lithium hydrogen phthalate crystals are presented in Fig. 
5. The nonlinear refractive index (n2) of the crystal was calculated using the standard relations given below :( M. 
Sheik-Bahae, et al. 1989; J.L. Bredas et al. 1994; J.J. Rodrigues et al.2002)  
Where S= 1- exp (-ra2/ωa2) is the aperture linear transmittance (0.01), ∆ϕo is the on-axis phase shift. The 
on-axis phase shift is related to the third-order nonlinear refractive index by 
Where k = 2π/λ, Leff = [1-exp(-αL)]/ α is the effective thickness of the sample, α is the linear absorption 
coefficient, L the thickness of the sample, Io is the on-axis irradiance at focus and n2 is the third-order nonlinear 
refractive index.
Nonlinear refractive index (n2) of the LHP  was calculated as 3.317x10
-11cm2/W the value of nonlinear absorption coefficient has been found to be β ~ 5.789x10-3cm2/W and nonlinear parameter are tabulated in table 3. 

  • solution Crystal growth
  • single crystal XRD
  • FTIR
  • thermal analysis
  • UV-Vis-NIR
  • Z-scan and nonlinear optical materials

Friday, September 5, 2014

Solution-processed, Self-organized Organic Single Crystal Arrays with Controlled Crystal Orientation

A facile solution process for the fabrication of organic single crystal semiconductor devices which meets the demand for low-cost and large-area fabrication of high performance electronic devices is demonstrated. In this paper, we develop a bottom-up method which enables direct formation of organic semiconductor single crystals at selected locations with desired orientations. Here oriented growth of one-dimensional organic crystals is achieved by using self-assembly of organic molecules as the driving force to align these crystals in patterned regions. Based upon the self-organized organic single crystals, we fabricate organic field effect transistor arrays which exhibit an average field-effect mobility of 1.1 cm2V−1s−1. This method can be carried out under ambient atmosphere at room temperature, thus particularly promising for production of future plastic electronics.


The ongoing proliferation of electronic devices and growing concerns about increasing environmental burdens are leading to increasing demands for solution-based fabrication methods, which will contribute towards a sustainable society with their low carbon emissions. The use of soluble organic semiconductors enables fabrication of plastic electronic devices, such as organic field effect transistors (OFETs), organic light emitting diodes and organic solar cells, with both low cost and low energy consumption123. In particular, organic single crystals have been reported to exhibit high performance in OFETs because of the absence of grain boundaries and the resulting low defect density45678910111213141516. However, to integrate organic single crystals into practical devices as active materials two techniques must be developed. The first is the patterned growth of organic single crystals on desired regions, which is necessary for reducing the crosstalk among neighboring devices. For instance, Briseno et al. formed organic single crystal arrays on selective surface areas by exploiting the different surface properties of a pattern produced by a polydimethylsiloxane stamp, but these crystals were grown from the vapor phase17. Thereafter, several studies have been conducted on the formation and/or patterning of organic single crystals on a substrate by solution processes181920212223242526272829303132,333435. The second requirement is the ability to control the orientation of the organic crystals. Charge transport in organic crystals depends upon their orientation, due to their commonly having an anisotropic molecular arrangement16, which can lead to considerable variability in the electrical performance of devices. Therefore, the ability to control both the position and orientation of deposited crystals is essential for practical application of organic crystals to devices. Recently, Minemawari et al. demonstrated an inkjet printing process for fabricating single crystal films with the organic semiconductor dioctylbenzothienobenzothiophene (C8-BTBT)33. They have used a technique combining antisolvent crystallization and inkjet printing, resulting in the formation of highly uniform organic single crystal films at the desired locations, and OFETs with an extremely high average mobility of 16.4 cm2V−1s−1. In this method, crystal nucleation occurs due to the evaporation of solvent.
In this work, we develop a bottom-up method which enables aligned formation of organic single crystals on a substrate by self-assembly. The use of self-assembly as a driving force to form a mono-crystalline semiconductor layer is particularly promising for printable electronics technology, because it can be performed under ambient atmosphere at room temperature. Here we use C8-BTBT as the organic semiconductor, which tends to form one-dimensional crystal under solvent vapor. Our method is based upon the confinement effect induced by different surface wettabilities, where the organic crystals are grown in the narrow trenches to restrict the growth direction. Consequently, we develop a process for the direct formation of organic single crystals using a self-organised solution-based method with both their position and orientation being controlled. The spontaneous alignment of one-dimensional crystals is possible not only for organic semiconductors1827 but also for some inorganic materials363738, as long as the materials can create one-dimensional single crystal structure. We also demonstrate that this method can fabricate organic FETs. The devices exhibit an average field-effect mobility (μFET) of 1.1 cm2V−1s−1. The simplicity of the proposed method makes it a promising candidate for widespread adoption in future electronics based on single crystals.


Fabrication of organic single crystal arrays by self-organization with controlled crystal direction

In order to realize oriented growth of organic crystals, we employed polymer assisted solvent vapor annealing (PASVA)3234. C8-BTBT was used as the organic semiconductor material because as it has been shown to be a good candidate for creating one-dimensional rod-like structures with good air-stability and a high device mobility323439. The PASVA offers the advantage of being an all-solution process that can produce high-quality organic single crystals at room temperature. In a previous report, we demonstrate the direct formation of C8-BTBT single crystals on a polymer base film under solvent vapor32. This process relies on the solubility of the polymer base film, which allows semiconductor molecules to travel significant distances on the surface. Consequently, PASVA enables the reorganisation of molecules into single crystals with lengths of up to several hundred micrometers. C8-BTBT tends to form long rod-like crystals, the long axis of which corresponds to the [100] crystal direction. This method was carried out on a patterned substrate, limiting the growth direction of the crystals and allowing fine control of the crystal location and orientation over a wide area.
We first patterned the substrate surface into regions that were either wettable or unwettable by the organic semiconductor solution29303135. A silicon wafer with a 200-nm-thick silicon dioxide layer was used as the substrate. The solution-wettable surface regions were first produced by UV-ozone cleaning. As illustrated in Figure 1a, a photoresist pattern was formed by photolithography on the wettable surface. A fluoropolymer, CytopTM, was then spin-coated and annealed for 2 hours at 90°C. The photoresist was subsequently lifted off to form unwettable Cytop regions on the substrate enclosing a pattern of wettable trenches. At this stage, the thickness of the Cytop layer measured by a surface profilometer was approximately 100 nm. An anisole solution of C8-BTBT (1 wt%) and poly(methylmethacrylate) (PMMA, 2 wt%) was then applied to the substrate, resulting in trace amounts of the semiconductor solution entering the wettable trenches. As the anisole evaporated, a polycrystalline C8-BTBT film was formed on an underlying PMMA film by vertical phase separation (similar to that reported in Ref.29) exclusively in the trenches. The PASVA with chloroform was then carried out for 10 hours, causing the polycrystalline C8-BTBT films in the trenches to recrystallize into rod-like single crystals oriented along the trench directions. As shown in a cross section inFigure 1b, the typical thicknesses of the crystals and PMMA layers were 250 nm and 80 nm, respectively. Besides, without PMMA the crystals were not grown in the trenches, with the role of PMMA being to absorb the chloroform solvent, enabling C8-BTBT molecules to move easily for crystallization.

(a) Schematic outline of the fabrication of self-aligned organic single crystal arrays. The wettable trenches are formed by patterning an anisole-unwettable 100-nm-thick Cytop layer using a standard photolithographic technique. A solution of C8-BTBT/PMMA in anisole is applied but remains only in the wettable trenches, because the surrounding Cytop region repels it. During PASVA with chloroform, the C8-BTBT film becomes recrystallized into single crystal arrays with the same orientation. The insert is the molecular structure of C8-BTBT. (b) Organic single crystals fabricated by the present method. The polarized optical micrograph shows the crystals are fabricated only in the trenches and have the same crystal orientation. The surface profile shows that the typical thickness of the crystals is about 250 nm.

Thus, by patterning wettable areas on the surface and using PASVA, we successfully form an organic single crystal array with a single crystal orientation over a wide area. A polarized optical micrograph of the array is shown in Figure 2a. It can be clearly seen that the crystals are formed only in the trenches and that they have a similar color and brightness. This indicates that the technique allows good control of both the crystal position and orientation. An analysis of the optical micrographs showed that 83% of the 270 trenches were occupied by crystals, 98% of which were preferentially aligned with a certain crystal orientation. The remaining 17 % of empty trenches without C8-BTBT single crystals in the figure were likely caused by uncompleted crystal creation due to the lack of either PMMA or C8-BTBT molecules. Figure 2b shows polarized optical micrographs of crystals rotated 45° between each image with the diagonal and extinction positions. This observation confirms that the crystals have the same orientation as the patterned trenches. We also perform X-ray diffraction analysis of these aligned crystals to investigate their internal crystallinity, as shown in Supplementary information 1. From the diffraction signals obtained, it can be confirmed that the C8-BTBT molecules are stacked in the same direction [100] as we reported previously3234. Thus, it implies that the rod-like structure of crystals aligned is coincident with crystals in Ref.32. Consequently, polarized optical microscopic images and X-ray diffraction patterns suggest that the all the crystals are aligned with the same crystal orientation.

Figure 2: Organic single crystal arrays with controlled crystal orientation in large scale.

(a) Polarized optical micrograph of an organic single crystal array. (b) Optical micrographs of crystals with and without a polarizer. The polarized images show the diagonal and extinction positions of the crystals. The images were taken at the positions rotated 45° for each with the diagonal and extinction positions.

The polarized optical micrographs were taken at 1, 2, 5, and 20 min after the start of the PASVA process. The red-arrows are guides showing the [100] crystal orientation.

We also investigate the effect of trench geometry on the crystal formation process. Figure 4 shows optical micrographs of crystals formed by PASVA trenches of different lengths (L) and widths (W). All other fabrication conditions, such as the volume of organic semiconductor solution used and the annealing time, are exactly the same for all samples. We first examine crystal formation in trenches with different L and fixed W ( = 20 μm). As can be seen in Figure 4b, the crystal orientation is found to clearly depend on the trench geometry. For the case of a square trench (L = W = 20 μm), the crystal orientation is random. On the other hand, crystals tend to align along the long direction of the trench as L increases, which suggests that the trenches must be longer in one direction to effectively align crystals. We next examine the effect of varying W for sufficiently large L (Figure 4c). For W = 5 μm, no crystallization of C8-BTBT is found to occur in the trench, probably due to an insufficient amount of C8-BTBT and underlying PMMA in such a narrow trench or the un-wetting PMMA of in the very narrow trench. A slight improvement in the crystallization degree is observed for the samples with W = 7.5–10 μm. Some crystals are formed but they are too small to become aligned in the trench. For W = 15–20 μm, sufficiently large crystals are formed with a relatively small spread in orientation. The crystals are typically longer than 50 μm, with the largest being longer than 600 μm (Figure 4d). However, for W > 25 μm, the spread in orientations tends to increase, probably due to insufficient confinement within the trench. Consequently, a W value of around 20 μm can be considered to be the most appropriate for optimizing the degree of crystal orientation. In organic materials, C8-BTBT is one of the most promising candidates for this method for device application. However, we are confident that a controlled growth direction of other organic solution-processable single crystals such as BTBT derivatives, perylene-bis(dicarboximide) derivatives or trimethylsilane-aquarterthiophene is possible1827. In the case of other materials, the trench size and width need to be optimized.

Figure 4: Control of the crystal orientation by trench size on the substrate.
Control of the crystal orientation by trench size on the substrate.
(a) Schematic diagram of the trench geometry defined by the length (L) and width (d). (b) Optical micrographs of samples after crystal growth for different L and a fixed W of 20 μm. The black arrows indicate the [100] direction of the C8-BTBT crystals. (c) Optical micrographs of samples with the different W and sufficiently large L. (d) Polarized optical micrograph of the longest crystal obtained. The length of the crystal was 685 μm.
We next fabricate OFETs using the aligned single crystals fabricated by this method. The OFETs are fabricated with a bottom-gate top-contact structure as shown in Figure 5a. A highly doped Si substrate is used as a gate electrode, and the silicon dioxide and PMMA layers underneath the organic crystals act as a gate insulator. The long axis direction of the crystals corresponds to the[100] crystal orientation along which the largest π-orbital overlap among neighboring molecules is expected40. Since the highest occupied molecular orbital (HOMO) of C8-BTBT is known to be 5.7 eV, and a relatively large charge injection barrier is expected for gold source/drain electrodes, an amorphous iron (III) chloride (FeCl3) layer is inserted at the metal/organic interface. FeCl3 is known as a strong acceptor, which improves the charge injection efficiency. The charge injection barrier between the HOMO of C8-BTBT and Au is reduced by the acceptors, thereby inducing charge transfer between C8-BTBT and FeCl34142. Using this FeCl3/Au electrode configuration, 32 OFET devices are fabricated. Values of field effect mobility, threshold voltage and on/off ratio are extracted for the all devices fabricated and their distribution is shown in Figure 5b. Also, typical transfer and output characteristics of the devices are shown in Figure 5c and d, respectively. An average value of the mobility of 1.1 cm2V−1s−1 (standard deviation: 0.78 and maximum mobility: 3.8 cm2V−1s−1) is obtained. The mobility value is lower than our previous report32 and a recently published report by Minemawari et al.33 This would be due to the relatively short channel length used (35 μm) and the large contact resistance. The effect of the contact resistance can be seen in the output characteristics (Fig. 5d), where the drain current increases nonlinearly at the low drain voltage region. The large contact resistance is probably induced by the energy level mismatch between Fermi level of Au and HOMO of C8-BTBT or relatively large thickness of the crystals32, although we insert the acceptor layer to suppress these unfavorable effects. On the other hand, the devices show ideal transistor behavior in the transfer characteristics (Fig, 5c) with an average on/off ratio of 104, indicating a possibility to use our method for practical fabrication process in plastic electronics. Furthermore, the performance distribution exhibited is similarly narrow, as reported by organic field effect transistors, in terms of standard deviation323335. The simplicity of this method can be applied to other solution processable materials having an one-dimensional structure such as solution-processable zinc oxide3637 and lanthanide hydroxide nanorods38. Thus, this method is suitable to be used for the fabrication of single crystal arrays and provides a new solution-processing method to control the orientation of single crystals in many fields.

Figure 5: Organic single crystal field effect transistors.
Organic single crystal field effect transistors.
(a) A schematic diagram of the device structure and optical microscopic image of the transistor. (b) Histograms of field effect mobility: 1.1 cm2V−1s−1 (standard deviation: 0.78 and maximum mobility: 3.8 cm2V−1s−1), threshold voltage: −14.9 V (σ: 6.65) and log (on/off ratio) 4.0 (σ:0.82) measured 32 transistors. (b) Transfer and (c) output characteristics of a typical device.
In conclusion, we develop a solution-based method for the fabrication of organic single crystal arrays with controlled crystal orientation using PASVA in confined areas on the surface. We demonstrate that C8-BTBT crystals can be self-organized in patterned wettable rectangular regions on a substrate, and that the [100] crystal direction can be aligned along the long axis of the rectangle. The driving force is found to be the self-assembling ability of the C8-BTBT molecules on the soluble polymer base film. The influence of the geometry of the confinement area on the crystal alignment is also discussed. Moreover, OFETs based on the aligned crystals are demonstrated with an average field-effect mobility of 1.1 cm2V−1s−1 measured across 32 devices. These results indicate that the proposed technique is promising for future large-area electronics based upon all solution-processable single crystals.


Patterned Cytop Substrate

All experiments were carried out under ambient conditions. A highly doped n-type [100] silicon wafer with a 200-nm-thick SiO2 layer was used as a substrate. The wafer was cleaned with solvents and treated with ultraviolet (UV) ozone to make the surface wettable for organic solutions. Photoresist (PR, ma-N 1400, micro resist technology, Germany) was spin-coated on the substrate and patterned by a typical photolithographic technique. CytopTM (Asahi Glass, Japan) was diluted with the developer (CT-Solv. 180) at a ratio of 1:2 and spin-coated onto the PR patterned substrate. The substrate was annealed at 90°C for two hours. The PR was then lifted off, resulting in a patterned Cytop layer on the substrate. The thickness of the Cytop layer was measured to be about 100 nm using a surface profiler.

C8-BTBT Solution

C8-BTBT (Nippon Kayaku) and PMMA (Nippon Zeon, MW = 950,000) were dissolved in anisole (1 wt.% for C8-BTBT and 2 wt% for PMMA).

Aligned Crystal Growth

The C8-BTBT solution was applied to the patterned substrate, but remained only in the trenches due to their wettability, and PASVA was performed with chloroform vapor for 10 hours. The growth process is similar to the process described in Ref.32. Optical images, including the real-time images of the self-alignment process in Figure 3, were obtained using a digital optical microscope (VHX-1000, Keyence).

FET Fabrication and Characterization

OFETs were fabricated using the aligned crystals with the [100] crystal direction corresponding to the channel direction. Source and drain electrodes were thermally evaporated at a rate of 0.1 Å/s for FeCl3 (0.3 nm) and gold (40 nm) through a metal shadow mask in vacuum (under 5×10−4 Pa). The OFET characteristics were measured in vacuum (under 5×10−4 Pa) using an Agilent 4156C parameter analyzer. Ci (capacitance per unit area) measured by capacitance-voltage measurement is about 30 nFcm−2 at 50 Hz.


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