**3. Conclusions**

Takayasu arteritis continues to be a diagnostic challenge, mostly on the first-line of care, because other pathologies show similar clinical and laboratory findings and there is not a golden standard to diagnose it. In addition, the signs and symptoms are not usually the same in all patients, and it could even be an underdiagnosed disease.

On the other hand, treatment options for TA is an area in which progress has been shown in recent years. However, these options are not yet considered to be accessible to all patients.

This disease still has a field of study in terms of its pathophysiology, diagnosis, and treatment.


**6. Conclusions**

In this study, numerical analysis was performed using LS-DYNA for the behavior of a slab-column joint under an explosive load. The results of this study can be summarized as follows.

**Author Contributions:** Conceptualization, performing analysis, and writing—original draft, K.M.L. and J.H.L.; Writing—review and editing, D.G.Y., B.Y.L., and J.H.L.; supervision, J.H.L. All authors have read and agreed to the published version of the manuscript.

**Funding:** The paper was supported by the research grant of the University of Suwon in 2017.

**Acknowledgments:** The paper was supported by the research grant of the University of Suwon in 2017.

**Conflicts of Interest:** The authors declare no conflict of interest.


Advances and Challenges in Urine Laboratory Analysis

*Edited by Tomasz Jarzembowski and Agnieszka Daca*

## Advances and Challenges in Urine Laboratory Analysis

*Edited by Tomasz Jarzembowski and Agnieszka Daca*

Published in London, United Kingdom

Advances and Challenges in Urine Laboratory Analysis http://dx. doi. org/10. 5772/intechopen. 104336 Edited by Tomasz Jarzembowski and Agnieszka Daca

#### Contributors

Jorge Alberto Cortés, Laura Cristina Nocua-Báez, Kumar Venkitanarayanan, Abraham Joseph Pellissery, Poonam Gopika Vinayamohan, Leya Susan Viju, Divya Jopseph, Hiroko Furo, Sarah Abdelsayed, Tony Lin, Yi Yuan Zhou, Chandrasekhar Nagaraj, Noren Villalobos, Lovelesh K. Kumar Nigam, Agnieszka Daca, Tomas Jarzembowski

#### © The Editor(s) and the Author(s) 2024

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**4. Conclusions**

Stainless steel coatings with varying Ag contents were deposited in inert (Ar) and reactive (Ar and N2) atmospheres by means of magnetron sputtering and their structural, mechanical and tribological properties were studied. The study concludes the following:

BCC and FCC microstructures were exhibited by the coatings deposited in inert and reactive atmospheres, respectively. As for coatings deposited with silver, the FCC structure of silver was also evident. The coatings deposited in a nitrogen atmosphere and with a higher amount of Ag had a smaller crystallite size and higher values of deformation and lattice parameter.

Nanohardness values up to 8 GPa were obtained for the stainless steel coatings, corresponding to a significant increase in the hardness compared to the hardness of the AISI 316L steel used as substrate. The coatings with Ag and deposited in a reactive atmosphere exhibited a higher degree of hardness, which can be attributed to the fact that the use of nitrogen tends to stabilize the austenitic phase of stainless steel and cause an increase in the lattice parameter and the percentage of deformation, due to the supersaturation of nitrogen in the austenitic structure.

The COF in the produced coatings was reduced in comparison with the substrate. In the coatings deposited in a reactive atmosphere, there was a tendency to decrease the COF with an increase in silver content. This behaviour can be attributed to a good solid lubricant, Ag, which allows lubrication of the wear tracks of the film and friction pairs, so that the sliding between the two surfaces tends to decrease the friction coefficient of the coating.

Finally, the wear rates in the produced coatings were reduced in comparison with the substrate, which is associated with the significant increase in the hardness of the coatings. The coatings deposited with lower Ag content (Ar0Ag and ArN0Ag) have a lower value of the wear rate. The decrease in the wear resistance with the increase of Ag is possibly due to an increase in the fragility of the material, loss of adhesion, Ag aggregates, or debris formed on the wear track.

**Author Contributions:** C.L.E.P., A.A.C.R. and J.J.O. conceived and designed the experiments; C.L.E.P. performed the experiments; C.L.E.P., A.A.C.R. and J.J.O. wrote the paper.

**Funding:** This research was funded by National University of Colombia, project "Nanostructured coatings of FCC metallic alloys deposited via sputtering" (37535).

**Conflicts of Interest:** The authors declare no conflict of interest.


**Pulsed Laser Deposition of Indium Tin Oxide Thin Films on Nanopatterned Glass Substrates**

#### **Marcela Socol 1,\*, Nicoleta Preda 1,\*, Oana Rasoga 1, Andreea Costas 1, Anca Stanculescu 1, Carmen Breazu 1, Florin Gherendi 2 and Gabriel Socol 2**

Received: 5 December 2018; Accepted: 25 December 2018; Published: 29 December 2018

**Abstract:** Indium tin oxide (ITO) thin films were grown on nanopatterned glass substrates by the pulsed laser deposition (PLD) technique. The deposition was carried out at 1.2 J/cm2 laser fluence, low oxygen pressure (1.5 Pa) and on unheated substrate. Arrays of periodic pillars with widths of ~350 nm, heights of ~250 nm, and separation pitches of ~1100 nm were fabricated on glass substrates using UV nanoimprint lithography (UV-NIL), a simple, cost-effective, and high throughput technique used to fabricate nanopatterns on large areas. In order to emphasize the influence of the periodic patterns on the properties of the nanostructured ITO films, this transparent conductive oxide (TCO) was also grown on flat glass substrates. Therefore, the structural, compositional, morphological, optical, and electrical properties of both non-patterned and patterned ITO films were investigated in a comparative manner. The energy dispersive X-ray analysis (EDX) confirms that the ITO films preserve the In2O3:SnO2 weight ratio from the solid ITO target. The SEM and atomic force microscopy (AFM) images prove that the deposited ITO films retain the pattern of the glass substrates. The optical investigations reveal that patterned ITO films present a good optical transmittance. The electrical measurements show that both the non-patterned and patterned ITO films are characterized by a low electrical resistivity (<2.8 × 10−4). However, an improvement in the Hall mobility was achieved in the case of the nanopatterned ITO films, evidencing the potential applications of such nanopatterned TCO films obtained by PLD in photovoltaic and light emitting devices.

**Keywords:** PLD; ITO; nanoimprint lithography; coatings

#### **1. Introduction**

Transparent conductive oxides (TCO) have been intensively studied in recent years due to their applications in many technological areas, such as optoelectronics devices, automobile and aircraft windows, and antireflection coatings [1–4]. Among various metal oxides, ZnO, SnO2, In2O3, and CdO have been extensively used in organic optoelectronic devices such as organic photovoltaics (OPVs) and organic light-emitting devices (OLEDs) [1,5–7]. Due to its unique optical (high transparency) and electrical (low electrical resistivity) features, indium tin oxide (ITO) remains the most investigated TCO [2,3]. Other ITO properties are linked to surface roughness, work function, mechanical characteristics, and environmental stability. The attributes of ITO layers are strongly influenced by the deposition techniques involved in TCO fabrication [5], the most used methods being magnetron sputtering [8,9], oxygen ion beam assisted deposition [10,11], chemical vapor deposition (CVD) [12,13], and pulsed laser deposition (PLD) [14,15]. The PLD method results in TCO coatings with appropriate electrical and optical properties [1], with its major advantage being the preservation of the target chemical composition in the transferred films. Furthermore, PLD allows the deposition

of the films at low substrate temperature, thus making the technique suitable for the fabrication of TCO films even on plastic substrates [14]. In 2000, Ohta published a study regarding the PLD of an ITO layer characterized by a low electrical resistivity (7.7 × 10−5 Ω·cm) on an yttria-stabilized zirconia substrate [16]. In 2001, Suzuki reported the growth by PLD of an ITO film characterized by a lower electrical resistivity (7.2 × 10−5 Ω·cm), a transmittance in the visible part of the solar spectrum greater than 90%, and a very smooth surface (0.61 nm average surface roughness) [17]. For the preparation of ITO films with adequate optical and electrical properties, the most important parameters of PLD are the oxygen gas pressure and the substrate temperature. Thus, a decrease of the oxygen pressure (*P*O2 ) leads to an increase of the oxygen vacancy concentration in the ITO film, which has the consequence of increasing the carrier concentration and the conductivity of the deposited layer [18]. Because apparently the optical transmittance increases with the increase of the oxygen pressure [1], an optimum between optical and electrical properties must be achieved. A higher substrate temperature leads to the increase of grain size in the grown films, and, in this way, the grain boundary scattering is reduced and results in an increase of the conductivity of the ITO films [19].

In the last few years, some papers in the field of solar cells and OLEDs have focused on the improvement of device parameters using light out-coupling methods, approaches which imply the modification of substrates by patterning techniques [20–23]. For patterns fabrication, e-beam lithography [24], nanoimprint lithography (NIL) [25], and focused ion beam (FIB) [26] are the most frequently used techniques. NIL has been proven to be a powerful tool for the mass production of micro/nanostructures with controlled shape and density on different substrates like glass, Si wafers, and polymer films [27,28]. Moreover, the NIL technique provides an ideal solution for patterning large areas with good resolutions at low cost and high throughput [29]. This special peculiarity of NIL opens the way for many economically feasible applications regarding the deposition of ITO films by different routes on patterning substrates obtained by NIL. Despite this aspect of NIL, few research papers have been published on this subject [30–32]. Hence, ITO films were grown by PLD on thermal nanoimprinted glass plates using self-organized nanopattern molds of oxides (NiO, α-Al2O3) [30,31] and on patterned glass substrates heated at 200 ◦C [32].

In this context, the present work is focused on the PLD (unheated substrate and using a lower laser fluency) of ITO films on nanopatterned glass substrates fabricated by NIL. ITO layers were also deposited by PLD on flat glass substrates for evidencing the influence of the patterns on the properties of the nanostructured ITO films. The structural, compositional, morphological, optical, and electrical properties of both non-patterned and patterned ITO films were investigated and analyzed in a comparative manner. The information from this research can be helpful for developing potential applications of such patterned TCO films in organic optoelectronic devices.

#### **2. Experimental Section**

The patterns were fabricated on glass substrate with the UV nanoimprint lithography (UV-NIL) method using an EVG 620 mask aligner (EV Group, Sankt Florian, Austria). The following steps were involved in the patterning process: (i) the glass substrate was preheated at 150 ◦C for 2 min; (ii) the primer was spin-coated (Brewer Science Cee 200X Spin Coater, Brewer Science, Inc., Rolla, MO, USA) to improve the adhesion of the polymer photoresist layer; (iii) the UV-resist layer was deposited by spin-coating and further annealed at 120 ◦C for 30 s; (iv) the soft stamp (mold) with the desired pattern was placed on the photoresist layer and pressed at a uniform contact pressure of 100 mbar; (v) the photoresist layer was exposed to UV light for 90 s, allowing the cross-linking process to lead to its solidification; and (vi) the soft mold was released, which left the UV-resist pattern [25]

The ITO films were deposited on flat and nanopatterned glass substrates by the PLD technique using an excimer laser source with krypton fluoride, KrF (CompexPro 205, 248 nm wavelength, τFWHM ~25 ns, Coherent Inc., Santa Clara, CA, USA) operating at 10 Hz repetition rate. A solid ITO target (SCI Engineered Materials Inc., Columbus, OH, USA, In2O3:SnO2 = 90%:10% weight) was ablated with 7000 laser pulses. The laser beam was directed on the target surface at 45◦ incidence angle with a MgF2 lens (300 mm focal length) placed outside of the deposition chamber. The distance between target and substrate was fixed at 5 cm, and the target was rotated during the deposition to prevent its local damage. The deposition chamber—having 10−4 Pa residual pressure—was filled with oxygen 6.0 up to 1.5 Pa pressure. The *P*O2 was chosen by taking into account that ITO films with low resistivity value can be grown at room temperature (RT) using this pressure value [19]. The deterioration of the patterned nanostructures was avoided by using low laser fluency (1.2 J/cm2) and maintaining the substrates at RT. More details about the PLD experimental set-up are given in our previous papers [33,34].  In addition to the samples already mentioned, a second specimen based on nanopatterned glass substrate coated with ITO (ITO/NP-glass\_bis) was also analyzed to emphasize the reproducibility of this preparation procedure combining UV-NIL and PLD techniques.

The thickness of the deposited ITO/glass films (as average median between the values obtained from three different measurements) was evaluated at ~340 nm using an XP 100 profilometer (Ambios Technology, Inc., Santa Cruz, CA, USA).

The prepared samples were studied from structural, morphological, optical, and electrical points of view. The crystalline structure was analyzed using a D8 Advance (Bruker AXS, Karlsruhe, Germany) instrument operating with Bragg-Brentano geometry with a monochromatized Cu Kα1 radiation (λ = 1.4506 Å). The diffractograms were recorded in the 20◦–80◦ range using 0.02◦ step size and 2 s/step. The morphology and the elemental composition were observed using a Zeiss Merlin Compact field emission scanning electron microscope and a Gemini SEM 500 (Zeiss, Oberkochen, Germany) field emission scanning electron microscope equipped with energy dispersive X-ray analysis Quantax XFlash detector 610 M (Bruker*,* Billerica, MA, USA)as an accessory. The roughness was evaluated using a MultiView 4000 atomic force microscope (phase feedback, Nanonics Imaging Ltd., Jerusalem, Israel). The optical properties were investigated by UV-VIS spectroscopy and photoluminescence (PL) using a Carry 5000 Spectrophotometer (Varian, Inc., Palo Alto, CA, USA) and a FL 920 spectrometer (Edinburgh Instruments Ltd., Livingston, UK) with a 450 W Xe lamp excitation and double monochromators on both excitation and emission, respectively. The optical measurements were made at room temperature. The transmission spectra were recorded in the 200–1100 nm domain, and the PL spectra were acquired at λexc = 335 nm (350–650 nm range) and at λexc = 435 nm (450–850 nm range). The parameters for recording were as follows: slit size = 3 mm, step size = 1 nm, and dwell time = 0.25 s. The carrier transport properties were evaluated from the measurements carried out at room temperature using a H50 Hall effect/Van der Pauw system (version, MMR Technologies Inc., San Jose, CA, USA).

#### **3. Results and Discussions**

The elemental composition of the TCO films grown by PLD was evaluated by energy dispersive X-ray analysis (EDX), which is presented in the Figure 1. The EDX spectra of ITO/glass and ITO/NP-glass samples evidenced the presence of In, Sn, and O components. In both cases, the atomic percentage for Sn:O:In was found to be about 3.7:63.5:32.7, confirming that the PLD target composition was maintained in the deposited ITO film. The results are in agreement to those reported for ITO films obtained by PLD [35], as the technique allows a stoichiometric transfer of the material from the target to the deposited film. The other peaks observed in the EDX spectra originated from the glass used as deposition substrate.

**Figure 1.** Energy dispersive X-ray analysis (EDX) spectra of indium tin oxide ITO/glass and ITO/nanopatterned (NP)-glass samples.

As mentioned above, substrate temperature and oxygen pressure have determinant impact on the crystalline structure of the TCO films grown by PLD. Thus, the ITO/glass and ITO/NP-glass samples were investigated by X-ray diffraction (XRD). In Figure 2, the XRD patterns of the ITO films deposited on unheated substrates exhibit only a broad peak at ~31◦ which can be related to a microcrystalline structure with a preferred (222) orientation [36]. The result is consistent with other studies carried out on ITO films prepared by PLD at RT and low *P*O2 , though with higher laser fluency (4 J/cm2) [37]. It was noticed that the patterning process has no influence on the ITO crystallinity.

**Figure 2.** X-ray diffraction (XRD) patterns of glass, ITO/glass and ITO/NP-glass samples.

Also, the morphology and the roughness of the TCO thin films are key features which influence their optical and electrical properties. Ergo, in the next step, all prepared samples were analyzed by field emission scanning electron microscopy (FESEM) and atomic force microscopy (AFM). These types of analyses for ITO/glass, NP-glass, ITO/NP-glass, and ITO/NP-glass\_bis can be seen in Figures 3–6, respectively.

**Figure 3.** Field emission scanning electron microscopy (FESEM) images at different magnifications (**A**,**B**,**C**) and atomic force microscopy (AFM) images (**D**,**E**) in 2D and 3D format of the ITO/glass sample.

**Figure 4.** FESEM images at different magnifications (**A**,**B**,**C**) and AFM images (**D**,**E**) in 2D and 3D format of the NP-glass sample.

**Figure 5.** FESEM images at different magnifications (**A**,**B**,**C**) and AFM images (**D**,**E**) in 2D and 3D format of the ITO/NP-glass sample.

**Figure 6.** FESEM images at different magnifications (**A**,**B**,**C**) and AFM images (**D**,**E**) in 2D and 3D format of the ITO/NP-glass\_bis sample.

The FESEM images of the ITO films deposited on flat glass substrate (Figure 3) disclose a smooth surface in accordance with observations reported in the case of ITO films prepared by solution-based fabrication methods [38].

In the case of the structures fabricated by UV–NIL on glass substrates, the FESEM images (Figure 4) show arrays of periodic pillars with diameters of ~350 nm and a distance between the pillars of ~1100 nm. As can be seen in Figures 5 and 6, the deposition of the ITO by PLD resulted in the increase of the pillars' width and the decrease of the separation step—the deposited films were trying to fill the space between pillars and to cover them.

Using the AFM investigations, the root mean square (RMS) parameter was evaluated as being: 1 nm for ITO/glass (Figure 3), 59 nm for NS-glass (Figure 4), 47 nm for ITO/NP-glass (Figure 5), and 44 nm for ITO/NP-glass\_bis (Figure 6). The presence of the pillars lead, as was expected, to a roughness increase. In the case of the ITO/glass sample, the RMS value is lower in comparison with other values calculated for ITO films prepared by other methods [8], but it is comparable with those reported for ITO films grown by PLD, as this technique offers the possibility to obtain TCO films with a smooth surface when the deposition is made at low temperature and with a low laser fluency [19,39].

Additionally, the surface kurtosis (*R*ku) parameter, a peakedness indicator—also determined by AFM—has the following values: 5.2 for ITO/glass, 2.1 for NP-glass, 2.3 for ITO/NP-glass, and 2.4 for ITO/NP-glass\_bis. Based on the *R*ku values, it can be mentioned that the ITO/glass film presents more peaks than valleys, while the ITO/NP-glass films present more valleys than peaks.

The EDX mapping images of the ITO films deposited on both flat (Figure 7A,B) and nanopatterned glass (Figure 7C,D) substrate illustrate a uniform distribution of the chemical elements Sn, O, and In contained in the PLD target. Over the fabricated pillars, no preferential arrangement of the elements as clusters is evidenced.

**Figure 7.** FESEM (**A**,**C**) and EDX mapping (**B**,**D**) images of ITO/glass (**A**,**B**) and ITO/NP-glass (**C**,**D**) samples.

The height of the pillars obtained by UV-NIL was estimated at ~250 nm from the cross-sectional FESEM images shown in Figure 8A,B, as the height was reduced after their coating with ITO films Figure 8C,D. Furthermore, these FESEM images emphasize an interesting aspect: the shape of the pillars is changed after the deposition of the TCO towards a pyramid trunk-like shape.

**Figure 8.** Cross-sectional FESEM images at two magnifications of NP-glass (**A**,**B**) and ITO/NP-glass (**C**,**D**) samples.

The optical properties are presented in Figures 9 and 10. The ITO film deposited on flat glass substrate presents a transmittance over 80% between 600 and 1100 nm, with the interference maxima and minima exhibited in the visible range being typical for the films with similar thickness (~340 nm) deposited by PLD or by magnetron sputtering [8,19]. The interference characteristics are also observed in the UV-VIS spectra of the ITO film deposited on nanopatterned glass substrate. Using these maxima and minima and the Swaneopel method [40], the refractive index (*n*) value was evaluated at ~1.9 for ITO/glass—a characteristic value for the ITO films deposited by PLD—and at ~2.4 for ITO/NP-glass. Some studies reported that the n value depended on the substrate temperature, since higher values were obtained for the ITO films prepared at a low temperature [19]. In addition, by plotting (α*h*ν) 2 versus photon energy, the band gap values for both ITO/glass and ITO/NP-glass samples were estimated at ~3.65 eV and ~3.21 eV, respectively. The band gap of ITO deposited on flat glass substrate is thickness-dependent and is in accordance with other reported films prepared by PLD with different SnO2 content (5% or 10%) [37,39]. It is well known that ITO is a semiconductor with a direct wide band gap greater than 3 eV [3]. The increase of this value is usually attributed to the increasing of the carrier density, a process known as Burstein-Moss effect [19]. Regarding the lowering of the band gap value of ITO film deposited on the nanopatterned glass substrate, a similar effect, related to oxygen deficiency, was observed for the ITO deposited by spin-coating on self-assembled polymer nanopattern [41].

**Figure 9.** UV-VIS spectra and (α*h*ν) 2 vs. E dependency of ITO/glass and ITO/NP-glass samples.

**Figure 10.** Photoluminescence (PL) spectra at two excitation wavelengths of glass, NP-glass, ITO/glass and ITO/NP-glass samples.

The PL spectra of all investigated samples—recorded at two excitation wavelength (335 and 435 nm)—are shown in Figure 10, as such information is useful for the TCO applications in OPV or OLED devices [42]. Under UV excitation (335 nm), the ITO/glass sample revealed a structured emission band with peaks at about 410, 430, and 460 nm which can be attributed to the ITO [25,43]. Generally, these emissions are characteristic of ITO, appearing due to the In2O3 oxygen deficiencies [44]. However, it is difficult to make an assignment, since the glass substrate presents also a similar emission. The ITO/NP-glass sample disclosed a shift of the structured emission band compared with that of the NP/glass sample. Furthermore, the shoulder at about 500 nm can also be associated with the ITO emission [45]. Under visible excitation (435 nm), an emission band peaked at about 550 nm is evidenced by the ITO/glass sample being narrower in comparison with that of the glass substrate [46]. In the case of the patterned samples, the PL spectra near the emission band at 550 nm show another weak broad emission band between 600 and 800 nm, which can be as also related the deposited ITO film [46].

The electrical properties of the ITO films deposited on flat and nanopatterned glass substrate by PLD were evaluated from the Hall measurements (Table 1), which revealed that the electrons are the charge carriers.

The calculated electrical resistivity is lower for the ITO/glass sample in comparison with the values for ITO/NP/glass and ITO/NP-glass\_bis samples. Therefore, ITO samples prepared by PLD on substrates maintained at RT have resistivity values close to those reported for the ITO films deposited by PLD using a heated substrate (300 ◦C)—a target with 5% SnO2, with the TCO film having 30 nm in thickness [17]. Our ITO samples are also similar to ITO films deposited using a 1 Pa O2 atmosphere, a target having 10% SnO2 content and different temperature substrate (beginning from 100 ◦C) [39,47]. In addition, the resistivity of the ITO/glass sample has a better value (1.8 × 10−4 Ω·cm) relative to others obtained in similar PLD experimental parameters (substrate kept at RT, SnO2 content, oxygen pressure) [48]. As mentioned above, the oxygen pressure is a key parameter in the PLD, as it influences the resistivity value of the TCO films—an influence owing to the number of formed oxygen vacancies in the laser transferred ITO films [25]. Thus, the electrical resistivity decreases with the increase of the SnO2 content over 5%. The increasing of the Sn amount leads to a higher concentration of the electron traps [19]. In our case, the ITO/glass sample has the highest carrier concentration (3.3 × 1021 cm−3), the values of the ITO/NP-glass and ITO/NP-glass\_bis samples being similar. The results are in consensus with other results obtained for ITO samples prepared on heated substrate [19,48]. Also, in these studies, the carrier density is related to the Sn quantity, an increase in the carrier density being reported as effect of the Sn donor electrons for the samples grown from the target containing a higher Sn concentration [19]. The carrier density is connected to the band gap value: ITO/glass samples that featured the highest carrier density had *E*g = 3.65 eV, whereas ITO/NP-glass characterized by a lower carrier density has *E*g = 3.21 eV. Furthermore, an increase in the Hall mobility was evidenced for the ITO/NP-glass and ITO/NP-glass\_bis samples—15.1 and 14.6 cm2/Vs, respectively—compared to the ITO/glass sample—10.6 cm2/Vs—which has smaller values than other reported values [25] due to the carrier-carrier scattering as an effect of high carrier density [1]. Taking into consideration that the only difference between the samples investigated in this study was the use of different substrate type, the increase in the Hall mobility for the ITO films deposited by PLD on nanopatterned glass is clearly owed to this patterned substrate.

#### **4. Conclusions**

PLD is an adequate technique to deposit ITO films on both flat and patterned glass substrates at room temperature, 1.2 J/cm2 laser fluency, and low oxygen pressure (1.5 Pa). The patterned substrates containing periodic pillars with ~350 nm in width, ~250 nm in height, and ~1100 nm separation step were fabricated by a UV-NIL process. The EDX analysis confirms that the laser-deposited ITO films preserve the stoichiometry of the solid ITO target (In2O3:SnO2 = 90%:10% weight), and the XRD data show a (222) preferential orientation for the grown film. The SEM and AFM images prove that the deposited ITO films retain the pattern of the glass substrates, while the nanopatterned TCO films featured a good optical transmittance. A low RMS value (1 nm) was estimated for the ITO film deposited on flat glass. The optical band gap and the refractive index were evaluated from the UV-VIS spectra, and the obtained values were in agreement with other results reported for ITO films deposited by PLD. The electrical measurements revealed that a *n*-type semiconductor was obtained, as the TCO films were characterized by a low electrical resistivity (<2.8 × 10−4) regardless the substrate type. However, an increase in the Hall mobility was observed in the case of the ITO films deposited on nanostructured glass. By combining UV-NIL—a cost-effective technique to fabricate nanopatterns on large areas—and PLD, a method for growing TCO films at low substrate temperature can be obtained for nanopatterned ITO films. This could have applications in organic photovoltaic cells or organic light emitting devices.

**Author Contributions:** Conceptualization, M.S.; Methodology, M.S. and N.P.; Validation, M.S., N.P. and G.S.; Formal Analysis, A.C., F.G. and G.S.; Investigation, A.C., N.P., G.S., F.G., O.R. and C.B.; Resources, G.S. and A.S.; Writing—Original Draft Preparation, M.S.; Writing—Review and Editing, N.P. and F.G.; Supervision, G.S. and A.S.

**Funding:** This research was funded by the Romanian Ministry of Research and Innovation through National Core Program from PN18-110101 and LAPLAS V (3N/2018) contracts and from ROSA STAR 179/2017 contract.

**Conflicts of Interest:** The authors declare no conflict of interest.

#### **References**

© 2018 by the authors. Licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution (CC BY) license (http://creativecommons.org/licenses/by/4.0/).


**2. Definition and etiology of familial hypercholesterolemia**

Familial hypercholesterolemia (FH) is a genetic and metabolic disorder that affects the metabolism of cholesterol [1–10].

Currently, the genes involved in HF are the following: low-density lipoprotein receptor (LDLR) gene, apolipoprotein B-100 (APOB) gene and proprotein convertase subtilisin kexin type 9 (PCSK9) gene, LDLR adaptor protein 1 (LDLRAP1) gene [1–10]. See **Table 1**.

The mutation in LDLR gene, APOB gene and PCSK9 gene is inherited following an autosomal dominant/autosomal co-dominant pattern and the mutation in LDLRAP1 gene is inherited following an autosomal recessive pattern [1–10].

Mutations of the genes cause defective LDL uptake and degradation, which in-turn leads to an elevation of plasma low-density lipoprotein-cholesterol (LDL-C) level, producing the hypercholesterolemia phenotype. The chronic exposure to high levels of LDL-C lead to the development of atherosclerosis and cardiovascular disease at an early age [1–10].

**Table 1.**

*Genes involved in familial hypercholesterolemia.*

Two main types of HF are distinguished: heterozygous familial hypercholesterolemia and homozygous familial hypercholesterolemia. Heterozygous familial hypercholesterolemia is usually caused by a single pathogenic variant in one of the genes associated with familial hypercholesterolemia, mostly in LDLR. Homozygous familial hypercholesterolemia is caused by biallelic pathogenic variants, generally in LDLR [1–10].


*3.4.FractureCharacteristics*

**Table 3.** Elongation and yield strength of the welded joints without and with PWHT.

Figure 9 represents the fracture surface images of the joints without and with PWHT of 730 ◦C. The fracture of the as-welded joint occurred in the weldment; the failed surface contained cleavage fracture characteristics and it is considered to be a mainly brittle fracture. In all cases investigated for PWHT, the weld seam was strengthened and CB2 steel became a weak part, causing fractures that occurred in the CB2 side. The post fracture microstructures of the joints were similar and there were many dimples on the fracture surface. The results indicate that the PWHT process improved the microstructure and mechanical properties of the weldment, thereby avoiding brittle fracture at the weld.

**Figure 9.** Typical fracture surface SEM images of the joints: (**a**) without PWHT and (**b**) with PWHT, at 730 ◦C for 2h.

## **4. Conclusions**

In this paper, the microstructures and mechanical properties of the weldment between G115 and CB2 steels without and with PWHT were studied. The related conclusions can be drawn as follows:

**Author Contributions:** J.X. (Jiankun Xiong), X.Y., J.Y., L.Y., and J.X. (Jian Xu) formulated the original problem, designed the study, developed the methodology, and wrote the manuscript. J.X. (Jiankun Xiong), T.L., X.Y., G.M. and J.X. (Jian Xu) performed the welding, testing, characterization and collected data. J.X. (Jiankun Xiong) and G.M. controlled the materials selection. J.X. (Jiankun Xiong) and X.Y. provided guidance and interpretation of data. All authors have read and agreed to the published version of the manuscript.

**Funding:** This work was financially supported by the Sichuan Deyang Open University-City Cooperative Technology Research and Development Project (Project No.: 2018CKJ004) and the Sichuan Deyang Industry-University-Research Cooperation Technology R&D Project (Project No.: 2019CK094). This research was also supported by the fund of Sate Key Laboratory of Long-life High Temperature Materials (Project No.: DTCC28EE190934).

**Conflicts of Interest:** The authors declare no conflict of interest.


**Author details**

Ortigoza Daniel Víctor1,2

1 Committee on Arrhythmias and Electrophysiology of the Argentine Federation of Cardiology (AFC), Argentina

2 Medical Emergencies of the Lebanese Syrian Hospital, Buenos Aires, Argentina

\*Address all correspondence to<EMAIL_ADDRESS>
© 2022 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution License (http://creativecommons.org/licenses/by/3.0), which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

*Use of Non-Vitamin K-Dependent Oral Anticoagulants in Elderly and Fragile Patients… DOI: http://dx.doi.org/10.5772/intechopen.103033*


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