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Article

Effects of Nanoscale Morphology on Optical Properties of Photoluminescent Polymer Optical Fibers

by
Edith Perret
1,2,*,
Konrad Jakubowski
1,
Manfred Heuberger
1 and
Rudolf Hufenus
1
1
Laboratory for Advanced Fibers, Empa, Swiss Federal Laboratories for Materials Science and Technology, Lerchenfeldstrasse 5, 9014 St. Gallen, Switzerland
2
Center for X-ray Analytics, Empa, Swiss Federal Laboratories for Materials Science and Technology, Überlandstrasse 129, 8600 Dübendorf, Switzerland
*
Author to whom correspondence should be addressed.
Polymers 2022, 14(16), 3262; https://doi.org/10.3390/polym14163262
Submission received: 2 June 2022 / Revised: 19 July 2022 / Accepted: 26 July 2022 / Published: 10 August 2022
(This article belongs to the Special Issue Structure-Property Relationships in Polymer Fibers)
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Abstract

:
Bicomponent photoluminescent polymer optical fibers (PL-POFs) have been melt-spun and in-situ drawn to different extents. The results suggest that scattering in the sheath can effectively increase the photoluminescent dye excitation probability in the fiber core. The core/sheath PL-POFs are made of a semi-crystalline fluoropolymer sheath of low refractive index (RI) and an amorphous cycloolefin polymeric core of high RI, which is doped with a luminescent dye. The axial light emission, as well as the guiding attenuation coefficients of the core/sheath PL-POFs, have been measured using a side-illumination set-up. The incident blue laser is down-converted to red light, which is re-emitted and partially guided by the core. The axial light emission is measured at the fiber tip as a function of the distance from the illumination position to the integrating sphere. It is demonstrated that the presence of a semi-crystalline sheath significantly enhances the axial light emission and that it also lowers the attenuation coefficient, compared to the emission and guiding properties of PL core-only fibers. Additionally, the attenuation coefficient has been found to be lower in more strongly drawn PL-POFs. Wide-angle X-ray diffraction and small-angle X-ray scattering experiments reveal structural differences in differently drawn PL-POFs that can be linked to the observed differences in the optical properties.

1. Introduction

Luminescent waveguides [1,2,3] have been successfully utilized as luminescent solar concentrators (LSCs) for photovoltaic cell enhancement [4,5,6], to amplify signal detection of free-space optical communication systems [7,8,9], or to design color-tunable decorative elements [10]. Luminescent waveguides, in the form of polymer optical fibers (POFs) [2,11], can be produced by melt-spinning [12,13,14], which is the most economical fiber spinning process. Photoluminescent (PL)-POFs contain a high refractive index (RI) polymer core, which is doped with a PL dye that down-converts (change of wavelength) and emits light. Typically, such a core is enclosed within a low-RI polymer sheath, since the sheath provides enhanced mechanical as well as optical stability. Note, that for bicomponent fibers, the material that surrounds the core is typically called ‘sheath’ and for POFs, it is sometimes also called ‘cladding’. In the remainder of this manuscript, the surrounding material is called ‘sheath’. In contrast to standard optical fibers, PL-POFs are able to collect light to a great extent from side-illumination and convert and guide the light to the tip of the fiber. An example of such a device is shown in Figure 1. A photoluminescent dye, Lumogen Red 305 (LR305), which is doped to the core of a PL-POF, absorbs blue light from side-illumination and emits down-shifted red radiation, which is guided axially towards the tip of the PL-POF by the total internal reflection at the core-sheath interface [15] (Figure 1). In the past, we have studied the luminescent properties of such PL-POFs for different core host materials, as well as optical conversion efficiencies for fiber bundles as a function of illumination angle [15].
The present motivation in the field is to optimize the optical properties of photoluminescent waveguides. Especially the intensity of luminescence measured at the fibers’ tip (axial emission) has been intensively studied in the past, since it defines the effectiveness of dope-dyed waveguides, e.g., in solar concentrator applications. A strategy to improve the axial emission is to maximize the interaction of incident light with the PL containing medium, by increasing the geometric optical path within the waveguide. This can be achieved by making use of light scattering, which is introduced in the form of scattering centers either outside or inside the waveguides. For example, to improve the emission intensity of planar LSCs, the excitation light has been passed through an additional scattering or diffusing frontal layer, thus increasing its interaction path with the PL containing medium [16,17,18,19]. Furthermore, adding scattering microspheres directly into the luminescent waveguide can also increase the performance of such LSCs [20]. The latter method is, however, accompanied by higher propagation losses, since microspheres also impede the guidance of the light. In polymeric waveguides [21], such as heat-processed polymer plates, the light scattering arises from crystalline structures (large spherulites) within the amorphous phase [22,23,24]. Different densities, and thus different RIs, of crystalline and amorphous regions constituting a semi-crystalline polymer [25,26] are responsible for the scattering of light. In the case of POFs, the thinness of the sheath material hinders the formation of large spherulites but smaller crystals, called lamellae, can be formed [27].
In this work, bicomponent melt-spinning [13] was utilized to prepare PL-POFs (as shown in Figure 1), where both the core and the sheath are processed simultaneously into a continuous filament [12,28,29,30,31,32]. Two PL-POFs of different draw ratios (i.e., the ratio between the winder and first take-up godet speed in m/min) have been prepared. The aim of this work was to study the impact of the semi-crystalline morphology of the sheath material on the axially emitted photoluminescence intensity (axial emission). PL-POFs serve as a benchmark and are cross-referenced with core-only fibers in order to isolate the effect of the scattering from the semi-crystalline sheath material onto the axial light emission. For this purpose, axial light emission was measured by side-illuminating both core/sheath PL-POFs as well as core-only PL-POFs with a blue laser. Using this side-illumination setup, it was possible to measure the axial emission from the fibers’ tip as a function of the distance from the illumination position and thus also determine axial guiding attenuation coefficients. In addition to axial light emission measurements, the nano-structural properties have been determined by measuring wide-angle X-ray diffraction (WAXD) and small-angle X-ray scattering (SAXS) [33,34,35,36,37,38] patterns of core/sheath and core-only fibers. Differences in the structural properties of PL-POFs due to different draw ratios are discussed and correlated to differences in axial light emissions.

2. Materials and Methods

2.1. Materials

Several thermoplastic polymers are suitable and commercially available [39,40] for a PL-POF core. We have chosen the cycloolefin (COP) polymer, which was previously identified as the best host material for a specific photoluminescent dye, Lumogen Red 305 (LR305), as the formation of dye aggregates is less pronounced in this material [15]. COP granulates (Zeonor 1020R, refractive index 1.53) were purchased from Zeon Europe GmbH, Düsseldorf, Germany. The photoluminescent dye, LR305 (BASF, Basel, Switzerland), was added to the COP core at a concentration of 0.01 wt.%. The terpolymer of tetrafluoroethylene, hexafluoropropylene and vinylidene fluoride polymer (THVP), has become a common choice for the sheath material of melt-processed POFs [12,15,29,31]. THVP is characterized by good transparency, low RI, good melt-spinnability, and semi-crystallinity [41]. THVP granulates (THVP 2030GZ, RI = 1.35) were purchased from 3M GmbH, Rüschlikon, Switzerland. Acetone and methoxyperfluorobutane were purchased from Sigma Aldrich, Buchs, Switzerland, in order to remove the sheath for subsequent studies of the optical and structural properties of the core material. All materials were used as provided without purification.

2.2. Bicomponent Melt-Spinning of PL-POFs

A bicomponent melt-spinning procedure [14,15] was used to prepare core/sheath PL-POFs with a COP core and a low-RI, semi-crystalline THVP sheath. The melt-spinning setup is illustrated in Figure 2.
Previously dried COP (core material) was tumble-mixed with 0.01 wt% LR305 and fed into an 18 mm diameter extruder. The extruder encompassed three heating zones, which were set to 180, 265 and 270 °C. The melt was then pumped into the spin pack at 10.5 cm3/min. The THVP (sheath material) was fed into a 14 mm extruder, which had three heating zones set to 100, 165 and 280 °C. The melt was pumped into the spin pack at a rate of 6 cm3/min. The fibers were melt-spun into a water bath followed by a drawing over four godets in series (Table 1). Two different draw ratios (ratio between the winder and take-up godet 1 speeds in m/min) have been applied, namely DR = 1.1 and DR = 1.6. The maximum achievable draw ratio for the POFs was limited by the amorphous core material, since stretching beyond 1.6 caused draw-induced microcracks.

2.3. Sheath Removal from POFs

In order to study the axially emitted photoluminescence intensity as well as the structure of the COP core alone (sheath removed), it was necessary to expose the COP core by dissolving the THVP sheath [42]. For this purpose, the fibers were immersed in a solution of acetone and methoxyperfluorobutane in equal proportions for 90 min at room temperature. The solution was constantly stirred during this procedure. The fibers were then removed from the solution and rinsed to remove any residues of THVP, and finally dried in air. Spectrophotometric control verified that the waste solution did not show any dye coloration, indicating that the procedure was selective on the sheath material and did not dissolve the dye-doped COP core. Fibers with removed sheath are labeled as ‘core-only’ in the remainder of the manuscript.

2.4. Axial Light Emission Measurements

To assess the efficiency of collecting the light from side-illumination and guiding it to the fiber tip, we have measured the axially emitted photoluminescence intensity with an integrating sphere, which was attached to a photomultiplier tube (Figure 3). Core/sheath or core-only fibers were fixed in a straight line, with one end being inserted inside the sphere, and fixed at its entrance with a small stripe of double-sided tape. To minimize light absorption in contact with the adhesive tape, especially for exposed fiber cores, a very small stripe (<1 mm) was used. A blue light-emitting diode (LED) with an emission peak at 455 nm (M455F3, Thorlabs, Germany) illuminated the fiber orthogonally to its axis via a glass optical fiber (M28L02, Thorlabs, Germany). Note that the fiber diameter is small compared to the absorption length within the polymer core at the excitation source wavelength. Thus the illuminated portion of the fiber can be approximated as a homogenous light source (plane-wave source) [43,44]. The LED was re-positioned along the fiber axis and the intensity of emitted photoluminescence was measured at selected distances (x = 10, 15 and 20 cm) between the LED and the integrating sphere (Figure 3).
To compare measured intensities of differently drawn core/sheath PL-POFs with different diameters, a normalized specific intensity (NSI) was defined. The normalized specific intensity divides the measured intensity by the cross-sectional area of the fiber core.
N S I x = I measured x A core  
Imeasured(x) is the measured light intensity for a specific distance, x, of the LED from the integrating sphere, and Acore is the cross-sectional area of the luminescent core. Note, that a correction accounting for trapping efficiencies [45] of core/sheath and core-only fibers, which are solely based on refractive indices of core and sheath materials, is intentionally avoided here. This way the observed differences in NSI values of core/sheath PL-POFs compared to core-only fibers can isolate the effect of the sheath material on the axial light emission.
Translation of the illumination point to at least two different distances from the emitting fibers’ tip allows calculation of the attenuation coefficient in [dB/m], in analogy to the so-called cut-back technique [41]:
α = − 10 Δ d log I 20 I 10
Here, I20 and I10 are the intensities measured at positions 20 cm and 10 cm away from the fiber tip, respectively, and Δ d = 0.2   m − 0.1   m = 0.1   m is the distance between these positions.

2.5. X-ray Measurements

Wide-angle X-ray diffraction (WAXD) and small-angle X-ray scattering (SAXS) patterns were measured from core/sheath and core-only fibers (without THVP sheath) in order to determine meso- and nano-scale structural details arising from the core and sheath, respectively. WAXD and SAXS patterns were recorded on a Bruker Nanostar U diffractometer (Bruker AXS, Karlsruhe, Germany) with a beam-defining pinhole of 300 μm, with Cu Kα radiation (λ = 1.5419 Å) and a VÅNTEC-2000 MikroGap area detector. WAXD and SAXS measurements were performed in two separate experiments with distances of 9.4 cm and 110.8 cm between the fiber and the active detector area, respectively. Single fibers were mounted on holders for all measurements. WAXD patterns have been recorded for 30 min and SAXS patterns for 77 min.

3. Results and Discussion

3.1. Dimensions of Core/Sheath PL-POFs

Microscope images (VHX-1000D, Keyence, Osaka, Japan) of the core/sheath PL-POFs with DR = 1.1 and DR = 1.6 are shown in Figure 4. The determined fiber dimensions (core radii, core areas, sheath thickness, outer PL-POF radii and PL-POF areas) are summarized in Table 2.
The ratio of the core area to the total fiber cross-section area is around 76% (diameters scale linearly under drawing). The average values and standard deviations of the fiber dimensions given in Table 2 have been determined from five measurements.

3.2. Axial Emission Properties

In order to isolate the impact of the semi-crystalline sheath material (THVP) on the axially emitted photoluminescence intensity, the light emission of both the core/sheath PL-POFs as well as of the core-only fibers have been compared. Photoluminescence intensities, Imeasured (x), normalized specific intensities, NSI(x) (Equation (1)), and attenuation coefficients, α (Equation (2)), have been determined with the optical emission method described in Section 2.4 (Figure 3). The measurements have been repeated five times and average values, as well as standard deviations, are summarized inTable 3. Note, that the concentration of the photoluminescent dye, LR305, in the COP core is for all fibers 0.01 wt.%. Thus, the magnitude of self-absorption (overlap of emission with absorption band) is expected to be identical in all fibers.

Impact of the Presence of a Semi-Crystalline Sheath Material onto Axial Emission

The following observations are made when comparing the optical properties of core/sheath PL-POFs with core-only fibers (Table 3):
  • NSI values of core/sheath PL-POFs are significantly higher than NSI values of core-only PL-POFs. These values depend on the light-incoupling and light-guiding ability of the fiber.
  • The attenuation coefficients of core/sheath PL-POFs are smaller than the ones of core-only PL-POFs. The smaller the attenuation coefficient, the less light is lost over a fixed distance along the fiber. Thus, the removal of the sheath material for core-only fibers induces additional attenuation.
The calculated NSI(x) from the measured intensities has been fitted to the following empirical function:
N S I f i t x = N S I 0 × ( 10 − α 10 · x )
NSI(0) is the normalizing specific intensity, which is a fitting parameter. The fitting function also includes the attenuation constant α (Equation (2)), and as boundary condition, the three calculated NSI(x) values from Equation (1) for x = 10, 15 and 20 cm. In Figure 5, the calculated NSI-values are plotted logarithmically together with the fitting curves (dashed lines) from Equation (3). The improvement parameter due to the sheath, Fsheath, is calculated as follows:
F s h e a t h = N S I f i t c o r e / s h e a t h x / N S I f i t c o r e − o n l y x
This parameter, Fsheath, reflects the improvement of the normalized axial emission at the fibers’ tip due to the presence of the sheath material; it is also a function of the distance of the illumination point to the detector. Note, that the Fsheath parameters are plotted logarithmically in Figure 5 on the right axis. For both types of PL-POFs, the parameter increases with increasing distance, x, and ranges from 3.7 to 6.1 (x = 10 to 20 cm) and from 4.2 to 6.8 for DR = 1.1 and 1.6, respectively.
To summarize, the sheath improvement parameters reveal that a semi-crystalline sheath material can provide a significant improvement in the normalized specific emission intensity. Note, that a similar effect of the sheath onto the axial emission has been observed for other types of PL-POFs, e.g., for a thermally drawn PL-POF, where the addition of a 20 µm thick, solution-processed acrylate sheath has been shown to improve the axial emission by a factor of 2.6, compared to the core-only fiber [46].
Higher NSI values (axial emission) of core/sheath PL-POFs, compared to core-only fibers, arise mainly due to differences in the in-coupling of the light. For core/sheath PL-POFs, the NSI values depend on the refraction events at the air/sheath interface and scattering events that take place in the sheath material due to the presence of crystals. Figure 6 schematically explains the improvement of the axial emission intensity due to the semi-crystalline sheath material. Refraction at the air/sheath interface and scattering events in the sheath material lead to prolonged optical pathways across the photoluminescent core, thus increasing the probability for light down-conversion with axial re-emission. Small crystals and crystalline domains in the sheath material act as light-scatters because of the discontinuities in the refractive index at the amorphous/crystalline phase boundaries. Various types of optical scattering phenomena can occur depending on the size of the scattering centers. For example, Rayleigh scattering occurs due to the presence of crystals that are much smaller than the incident wavelength (crystal diameter D < 1/10 λ, D < 45.5 nm) [47]. Mie-scattering, however, arises from micro-domains in the polymer sheath [25,47,48]. Mie-scattering becomes more intense in the forward direction and its scattering intensity increases with the size of the crystalline domains. In the case of Rayleigh scattering, however, the backward and forward scattering are similar in intensity. Along these lines, the nanostructure of the PL-POFs has been investigated with X-rays as discussed in Section 3.3 below.
Note, that in Figure 6 the absorption and re-emission events, due to the presence of the PL dye in the core, are not shown, since the focus lies on comparing the pathway of the optical light, which reflects the probability of the light interacting with the dye. Due to the complexity arising from a large number of possible light rays (refraction, scattering events), the schematic in Figure 6 is only a simplified representation of possible pathways of light rays. Two perspectives are considered:
  • A 2D-view of the transversal cross-section of a core/sheath PL-POF (Figure 6a) and a core-only fiber (Figure 6b). The incoming light is refracted at the air/sheath interface and crystals in the sheath material of a PL-POF deflect the incoming light in different directions. Thus in the case of PL-POFs, a large part of the incoming light interacts with the core. Note, that light that is transmitted transversely through the fiber can also be returned to the core via scattering events. In contrast, for core-only fibers (Figure 6b) some light rays pass the fiber without even interacting with the core.
  • A 2D-view of the longitudinal cross-section of a core/sheath PL-POF (Figure 6c) and a core-only fiber (Figure 6d). Forward-scattering crystals in the sheath material of a PL-POF deflect the light path, resulting in longer traveling distances, L, of the light inside the core, thus a higher probability of dye excitation. In contrast, the undeflected wave in a core-only fiber (Figure 6d), has an interaction path that is maximally equal to the fibers’ diameter d.
It is concluded that in the case of PL-POFs, the refraction events at the air/sheath interface and scattering events in crystals in the sheath material led to increased axial emission values due to the fact that more light is guided into the core, enhancing the PL dye excitation.
The optical measurements also show that the sheath material in PL-POFs is essential to minimize attenuation losses. The following factors may be the cause of lower attenuation coefficients of the core/sheath PL-POFs compared to core-only PL-POFs:
(1)
During sheath removal, the solvent may cause microcracks in the surface of the amorphous core, which in turn increases the attenuation [49].
(2)
In core/sheath PL-POFs, a robust optical interface between the two materials exists, making the waveguide less sensitive to the negative impact of external factors, such as dust particles that attach to the surface.
In PL-POFs, excitation light rays that leave the core (‘lost’ light) and do not fulfill the total internal reflection condition, are refracted at the core/sheath interface and enter the sheath material. For a semi-crystalline polymer material, these short-wavelength rays can be back-scattered into the core through, e.g., Rayleigh scattering due to crystals of a few tens of nanometers in size [25,48]. This back-scattering mechanism is particularly effective for the short-wavelength excitation light since the intensity of the scattered Rayleigh radiation is proportional to 1/λ4. Therefore, blue light is even more strongly back-scattered into the core than red light. These rays of blue light can then excite the dye and be down-converted to red light and re-emitted into guiding modes of the core.
Weiss [45] has put forward an equation to predict the trapping efficiencies of fluorescent core/sheath POFs. The trapping efficiency is defined by the ratio between the trapped (or guided) optical energy and the total energy emitted from fluorescence in the fiber core and it can be derived from the refractive indices, RI, of the core and sheath materials [45]:
η tr = 1 − R I sheath R I core 2
For PL-POFs, the refractive indices are RIsheath = 1.35 for the THVP sheath and RIcore = 1.53 for the COP core material, respectively. In the case of core-only fibers, however, the surrounding RI = 1.0 arises from the air. The calculated trapping efficiencies of the core/sheath POF is ηtr,POF~0.22 and the calculated trapping efficiency of the core-only fiber is ηtr_core-only~0.57. These values would suggest that thanks to a higher RI difference, core-only fibers are able to trap and guide more light to the end of the fiber tip than core/sheath fibers. This is in contradiction to our findings from optical measurements of the axial light emission, where we have observed the opposite trend; the PL-POFs show larger axial emission values than core-only fibers. The experimental results strongly indicate that it is necessary to take into account additional parameters, such as the ability of crystals in the sheath material to scatter and couple light into the core. As is shown by the experimentally observed sheath-induced improvement parameter, the presence of crystals in the sheath can significantly enhance the in-coupling of the light, as well as enhance the back-scattering of blue light into the core and thus effectively increase the optical trapping efficiency.

3.3. Structural Properties

To further characterize the crystalline morphology of the sheath that likely affects light scattering, we have performed WAXD and SAXS measurements on PL-POFs and core-only fibers. The measured (X-ray) scattering patterns are shown in Figure 7 for DR = 1.1 and DR = 1.6. The fiber draw ratio is expected to directly affect the crystalline morphology. A comparison of the WAXD and SAXS patterns of PL-POFs with the corresponding core-only fibers reveals that both PL-POFs consist of an amorphous core (COP) and a semi-crystalline sheath (THVP). This conclusion is drawn from the fact that SAXS patterns of core-only fibers (Figure 7b,d) do not show any scattering features arising from lamellar crystals, whereas SAXS patterns from PL-POFs show straight or tilted reflections (Figure 7a,c). The complete absence of the lamellar reflections in the SAXS patterns of the core-only fibers proves that the sheath has been completely removed. Additionally, the WAXD patterns of core-only fibers show a typical halo (Figure 7b), which reflects the amorphous nature of the COP core material. Interestingly, the WAXD pattern of the core-only fiber DR = 1.6 in Figure 7d shows an additional arc-shaped equatorial reflection, which signifies that part of the COP polymer chains became partially oriented along the fiber axis due to the higher draw ratio [29]. Such arc-shaped equatorial reflections have already been observed in different types of amorphous and also semi-crystalline polymer fibers in the past and have been identified to arise from a highly-oriented non-crystalline mesophase, Pnc [34,35,36,50]. To better visualize the differences between WAXD patterns from PL-POFs and core-only fibers, as well as between differently drawn fibers, we have extracted equatorial and azimuthal profiles. The equatorial profiles have been extracted by an azimuthal integration over ± 10° (see equatorial sector between red lines in Figure 7a). The azimuthal profiles are obtained by integrating between 2θ = 11–22° (see white rings in Figure 7a). All profiles are shown in Figure 8 and have been normalized by the core areas to account for the differences in scattering volume. Thus, the intensities arising from the THVP sheaths correspond to the difference in intensities between the profiles from PL-POFs and the corresponding profiles from core-only fibers. These differential intensities are shaded in grey and blue in Figure 8, respectively. PL-POFs exhibit a pronounced peak at around 2θ~17.7° on the equator (Figure 8a), which arises from crystals in the THVP sheath. This equatorial peak is more pronounced for fibers with DR = 1.6 due to the overlap with the underlying equatorial mesophase signal (Figure 8b, dotted blue curve) [13] and an increased crystallinity. The higher crystallinity of the sheath material in the PL-POF with DR = 1.6, compared to the PL-POF with DR = 1.1, is reflected by the difference in equatorial intensities of the PL-POFs and core-only fibers (inset of Figure 8a). Note, that the displayed sheath intensity of the PL-POF DR = 1.6 has been divided by its sheath area and multiplied by the sheath area of PL-POF DR = 1.1. Therefore, the difference in the intensities directly reflects the difference in crystallinity of the sheath.
An illustration of plausible structures of the THVP sheath and COP core material for the PL-POF fibers, DR = 1.1 and DR = 1.6, from the WAXD and SAXS patterns is shown in Figure 9. The THVP sheath of the PL-POF DR = 1.1 shows a straight ‘two’-point reflection SAXS pattern (Figure 7a), which arises from stacked parallel crystals that are arranged along the fiber axis (Figure 9a, left) [41]. Note, that in reality there are four reflections present in the SAXS pattern; two in the upper half of the SAXS image, which overlap along the transversal direction, and two overlapping reflections in the lower half of the SAXS image. The average long spacing (Lavg~12 nm, Figure 9a, left) between the crystals along the fiber axis is estimated from the location of the reflections along the meridian (parallel to the fiber axis) [51]. The lateral position of the reflections reflects the average lateral spacing between crystals, L12~42 nm (Figure 9a, left). The width of the crystals, perpendicular to the fiber axis, Davg (Figure 9a, left), varies and is estimated from the widths of the reflections to be on average around 13 nm [52,53]. The crystal average size suggests that Rayleigh scattering of visible light is indeed occurring in the sheath material. The WAXD pattern (Figure 7b) shows a halo, thus the COP core is amorphous (Figure 9a, right). For PL-POFs DR = 1.6, the SAXS reflections (Figure 7c), arising from crystals in the THVP sheath, are tilted away from the fiber axis and form an x-shaped four-point pattern. Such x-shaped patterns indicate that large parallel crystals become tilted away from the fiber axis and different long-spacings are introduced between these crystals [33,54,55] (Figure 9b, left). The COP core shows both an amorphous phase and mesophase (Figure 9b, right) in the WAXD pattern (Figure 7d).

3.4. Structure-Property Relationship Comparing Differently Drawn PL-POFs

In order to investigate whether normalized scattering intensities or attenuation coefficients for PL-POFs of different draw ratios (Table 3, Figure 5) are significantly different from one another, we have performed statistical Welch tests [56]. Average values are considered to be significantly different when the calculated p-value is smaller than 0.05 for a two-tailed test. It is found that the PL-POF with DR = 1.6 has
(i)
a significantly lower attenuation coefficient (α = 28.4 ± 4) than the PL-POF with DR = 1.1 (α = 32.6 ± 4), p = 0.012.
(ii)
a significantly higher NSI value (NSI = 1499 ± 117) than the PL-POF with DR = 1.1 (1312 ± 117) for x = 20 cm, p = 0.036.
Using WAXD and SAXS one can thus show that the following structural properties are different comparing PL-POFs DR = 1.6 with DR = 1.1; (i) the core of the PL-POF DR = 1.6 contains a mesophase, (ii) the crystallinity of the sheath is higher for DR = 1.6 than for DR = 1.1, and (iii) the crystals in the THVP sheath are tilted. All these structural differences may be responsible for the differences in the axial emission properties of PL-POF DR = 1.6.
Note, that the axial light emission and attenuation coefficients of differently drawn core-only fibers are not significantly different from one another (p > 0.05), which suggests that the presence of a mesophase in core-only fibers with DR = 1.6 is not significantly affecting the optical emission properties of the fibers. Therefore, the structural differences of the sheath material in differently drawn PL-POFs have to be mainly responsible for the differences in the optical emission properties. The slightly increased crystallinity in the sheath material of the PL-POF with DR = 1.6 may cause more (blue) light to be scattered back into the core through Rayleigh scattering, compared to sheath materials with lower crystallinity. Note, that the absolute crystallinity is difficult to be reliably determined using X-ray scattering, but for melt-spun semi-crystalline fibers, crystallinity values are typically below 50%.

4. Conclusions

PL-POFs are promising materials for light concentrators, luminescent assemblies, or decorative light-emitting textiles [10]. As such, their characterization as leaky, scattering waveguides is of eminent importance. In this article, core/sheath PL-POFs and corresponding core-only fibers have been side-illuminated with a blue laser and the axial light emission was measured. It was demonstrated that the addition of a semi-crystalline sheath can significantly improve the axial light emissions and lower attenuation coefficients of core/sheath PL-POFs compared to PL core-only fibers. A sheath-related improvement parameter was introduced that increased as a function of the distance of the side-illumination point to the integrating sphere. Refraction events at the air/sheath interface and scattering events at crystals in the sheath material have been identified to significantly enhance the in-coupling of blue light from side-illumination into the core, which in turn enhances the PL dye excitation probability leading to higher axial light emission values of PL-POFs. This finding is fundamentally remarkable since in conventional POFs, the scattering of light by the nanostructure of the sheath has no significant effect on the axial light emission due to the lack of light-conversion in PL dyes.
WAXD and SAXS experiments have confirmed that the THVP sheath is indeed semi-crystalline. The crystals in the sheath material have been found to be responsible for the Rayleigh scattering of blue light since the crystals have on average a width (perpendicular to fiber axis) of about 13 nm. Additionally, ‘lost’ blue light (light that leaves the core at angles different from the critical total reflection angle) can be scattered back into the core by the crystals in the sheath through Rayleigh or Mie scattering, enhancing the PL dye excitation probability and thus lowering the attenuation coefficients.
In this work, we have given an overview of possible reasons for the increased axial light emission under the side-illumination of core/sheath PL-POFs. To fully understand the exact mechanisms of how the semi-crystalline sheath (crystal sizes, orientation, crystallinity, sheath thickness, etc.) affects the light-incoupling and back-guiding, further extensive trials and analytics of different types of PL-POFs would have to be performed. For future studies, it would also be of interest to investigate the cross-sectional microstructure of the THVP material with, e.g., high-resolution Raman mapping [57], since crystalline domain sizes that are similar to the wavelength are expected to lead to Mie scattering.

Author Contributions

Conceptualization, K.J. and R.H.; methodology, K.J., E.P., M.H. and R.H.; software, K.J. and E.P.; validation, K.J. and E.P.; formal analysis, K.J. and E.P.; investigation, K.J.; resources, K.J.; data curation, K.J. and E.P.; writing—original draft preparation, K.J. and E.P.; writing—review and editing, M.H. and R.H.; visualization, K.J and E.P.; supervision M.H. and R.H.; project administration, R.H.; funding acquisition, M.H. All authors have read and agreed to the published version of the manuscript.

Funding

This research received no external funding.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data presented in this study are openly available in the Mendeley repository at DOI:10.17632/84ck2b45h9.1.

Acknowledgments

Authors would like to thank Benno Wüst for operating the spinning plant.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Roncali, J. Luminescent Solar Collectors: Quo Vadis? Adv. Energy Mater. 2020, 10, 2001907. [Google Scholar] [CrossRef]
  2. Jakubowski, K.; Huang, C.-S.; Boesel, L.F.; Hufenus, R.; Heuberger, M. Recent advances in photoluminescent polymer optical fibers. Curr. Opin. Solid State Mater. Sci. 2021, 25, 100912. [Google Scholar] [CrossRef]
  3. Papakonstantinou, I.; Portnoi, M.; Debije, M.G. The Hidden Potential of Luminescent Solar Concentrators. Adv. Energy Mater. 2021, 11, 2002883. [Google Scholar] [CrossRef]
  4. Parola, I.; Illarramendi, M.A.; Jakobs, F.; Kielhorn, J.; Zaremba, D.; Johannes, H.-H.; Zubia, J. Characterization of Double-Doped Polymer Optical Fibers as Luminescent Solar Concentrators. Polymers 2019, 11, 1187. [Google Scholar] [CrossRef] [Green Version]
  5. Correia, S.F.H.; Frias, A.R.; Fu, L.; Rondão, R.; Pecoraro, E.; Ribeiro, S.J.L.; André, P.S.; Ferreira, R.A.S.; Carlos, L.D. Large-Area Tunable Visible-to-Near-Infrared Luminescent Solar Concentrators. Adv. Sustain. Syst. 2018, 2, 1800002. [Google Scholar] [CrossRef]
  6. Huang, C.-S.; Jakubowski, K.; Ulrich, S.; Yakunin, S.; Clerc, M.; Toncelli, C.; Rossi, R.M.; Kovalenko, M.V.; Boesel, L.F. Nano-domains assisted energy transfer in amphiphilic polymer conetworks for wearable luminescent solar concentrators. Nano Energy 2020, 76, 105039. [Google Scholar] [CrossRef]
  7. Riaz, A.; Faulkner, G.; Collins, S. A Fluorescent Antenna for White Light Visible Light Communications. In Proceedings of the 2019 Global LIFI Congress (GLC), Paris, France, 12–13 June 2019; pp. 1–4. [Google Scholar]
  8. Peyronel, T.; Quirk, K.J.; Wang, S.C.; Tiecke, T.G. Luminescent detector for free-space optical communication. Optica 2016, 3, 787–792. [Google Scholar] [CrossRef]
  9. Portnoi, M.; Haigh, P.A.; Macdonald, T.J.; Ambroz, F.; Parkin, I.P.; Darwazeh, I.; Papakonstantinou, I. Bandwidth limits of luminescent solar concentrators as detectors in free-space optical communication systems. Light Sci. Appl. 2021, 10, 3. [Google Scholar] [CrossRef]
  10. Jakubowski, K.; Heuberger, M.; Hufenus, R. Melt-Spun Photoluminescent Polymer Optical Fibers for Color-Tunable Textile Illumination. Materials 2021, 14, 1740. [Google Scholar] [CrossRef]
  11. Beckers, M.; Schlüter, T.; Vad, T.; Gries, T.; Bunge, C.-A. An overview on fabrication methods for polymer optical fibers. Polym. Int. 2015, 64, 25–36. [Google Scholar] [CrossRef]
  12. Quandt, B.M.; Braun, F.; Ferrario, D.; Rossi, R.M.; Scheel-Sailer, A.; Wolf, M.; Bona, G.-L.; Hufenus, R.; Scherer, L.J.; Boesel, L.F. Body-monitoring with photonic textiles: A reflective heartbeat sensor based on polymer optical fibres. J. R. Soc. Interface 2017, 14, 20170060. [Google Scholar] [CrossRef] [Green Version]
  13. Hufenus, R.; Yan, Y.; Dauner, M.; Kikutani, T. Melt-Spun Fibers for Textile Applications. Materials 2020, 13, 4298. [Google Scholar] [CrossRef] [PubMed]
  14. Hufenus, R.; Yan, Y.; Dauner, M.; Yao, D.; Kikutani, T. Bicomponent fibers. In Handbook of Fibrous Materials; Jinlian, H., Kumar, B., Lu, J., Eds.; Wiley-VCH: Weinheim, Germany, 2018; p. 1. [Google Scholar]
  15. Jakubowski, K.; Huang, C.-S.; Gooneie, A.; Boesel, L.F.; Heuberger, M.; Hufenus, R. Luminescent solar concentrators based on melt-spun polymer optical fibers. Mater. Des. 2020, 189, 108518. [Google Scholar] [CrossRef]
  16. Debije, M.G.; Dekkers, W. Functionalizing the rear scatterer in a luminescent solar concentrator. J. Renew. Sustain. Energy 2012, 4, 013103. [Google Scholar] [CrossRef] [Green Version]
  17. Debije, M.G.; Teunissen, J.-P.; Kastelijn, M.J.; Verbunt, P.P.C.; Bastiaansen, C.W.M. The effect of a scattering layer on the edge output of a luminescent solar concentrator. Sol. Energy Mater. Sol. Cells 2009, 93, 1345–1350. [Google Scholar] [CrossRef]
  18. Wang, C.; Winston, R.; Zhang, W.; Jiang, L.; Pelka, D.; Carter, S. Performance of Organic Luminescent Solar Concentrator Photovoltaic Systems. AIP Conf. Proc. 2011, 1407, 163–167. [Google Scholar]
  19. Mateen, F.; Oh, H.; Kang, J.; Lee, S.Y.; Hong, S.-K. Improvement in the performance of luminescent solar concentrator using array of cylindrical optical fibers. Renew. Energy 2019, 138, 691–696. [Google Scholar] [CrossRef]
  20. Liu, H.; Li, S.; Chen, W.; Wang, D.; Li, C.; Wu, D.; Hao, J.; Zhou, Z.; Wang, X.; Wang, K. Scattering enhanced quantum dots based luminescent solar concentrators by silica microparticles. Sol. Energy Mater. Sol. Cells 2018, 179, 380–385. [Google Scholar] [CrossRef]
  21. Bunge, C.A.; Beckers, M.; Lustermann, B. 3—Basic principles of optical fibres. In Polymer Optical Fibres; Bunge, C.-A., Gries, T., Beckers, M., Eds.; Woodhead Publishing: Cambridge, UK, 2017; pp. 47–118. [Google Scholar]
  22. Hashimoto, T.; Todo, A.; Kawai, H. Light scattering from tilted two-dimensional spherulites. J. Polym. Sci. Part A-2 Polym. Phys. 1973, 11, 149–173. [Google Scholar] [CrossRef]
  23. Molnár, J.; Sepsi, Ö.; Erdei, G.; Lenk, S.; Ujhelyi, F.; Menyhárd, A. Modeling of light scattering and haze in semicrystalline polymers. J. Polym. Sci. 2020, 58, 1787–1795. [Google Scholar] [CrossRef]
  24. Bernland, K.; Goossens, J.G.P.; Smith, P.; Tervoort, T.A. On clarification of haze in polypropylene. J. Polym. Sci. Part B Polym. Phys. 2016, 54, 865–874. [Google Scholar] [CrossRef] [Green Version]
  25. Aldabaldetreku, G.; Bikandi, I.; Illarramendi, M.A.; Durana, G.; Zubia, J. A comprehensive analysis of scattering in polymer optical fibers. Opt. Express 2010, 18, 24536–24555. [Google Scholar] [CrossRef] [PubMed]
  26. Illarramendi, M.A.; Aldabaldetreku, G.; Bikandi, I.; Zubia, J.; Durana, G.; Berganza, A. Scattering in step-index polymer optical fibers by side-illumination technique: Theory and application. J. Opt. Soc. Am. B 2012, 29, 1316–1329. [Google Scholar] [CrossRef]
  27. Murthy, N.S.; Grubb, D.T. Deformation in lamellar and crystalline structures: In situ simultaneous small-angle X-ray scattering and wide-angle X-ray diffraction measurements on polyethylene terephthalate fibers. J. Polym. Sci. Part B-Polym. Phys. 2003, 41, 1538–1553. [Google Scholar] [CrossRef]
  28. Beckers, M.; Vad, T.; Mohr, B.; Weise, B.; Steinmann, W.; Gries, T.; Seide, G.; Kentzinger, E.; Bunge, C.-A. Novel Melt-Spun Polymer-Optical Poly(methyl methacrylate) Fibers Studied by Small-Angle X-ray Scattering. Polymers 2017, 9, 60. [Google Scholar] [CrossRef] [Green Version]
  29. Reifler, F.A.; Hufenus, R.; Krehel, M.; Zgraggen, E.; Rossi, R.M.; Scherer, L.J. Polymer optical fibers for textile applications—Bicomponent melt spinning from cyclic olefin polymer and structural characteristics revealed by wide angle X-ray diffraction. Polymer 2014, 55, 5695–5707. [Google Scholar] [CrossRef]
  30. Quandt, B.M.; Hufenus, R.; Weisse, B.; Braun, F.; Wolf, M.; Scheel-Sailer, A.; Bona, G.-L.; Rossi, R.M.; Boesel, L.F. Optimization of novel melt-extruded polymer optical fibers designed for pressure sensor applications. Eur. Polym. J. 2017, 88, 44–55. [Google Scholar] [CrossRef]
  31. Lustermann, B.; Quandt, B.M.; Ulrich, S.; Spano, F.; Rossi, R.M.; Boesel, L.F. Experimental determination and ray-tracing simulation of bending losses in melt-spun polymer optical fibres. Sci. Rep. 2020, 10, 11885. [Google Scholar] [CrossRef]
  32. Sohn, I.-S.; Park, C.-W. Diffusion-Assisted Coextrusion Process for the Fabrication of Graded-Index Plastic Optical Fibers. Ind. Eng. Chem. Res. 2001, 40, 3740–3748. [Google Scholar] [CrossRef]
  33. Perret, E.; Reifler, F.A.; Hufenus, R.; Bunk, O.; Heuberger, M. Modified Crystallization in PET/PPS Bicomponent Fibers Revealed by Small-Angle and Wide-Angle X-ray Scattering. Macromolecules 2013, 46, 440–448. [Google Scholar] [CrossRef]
  34. Perret, E.; Hufenus, R. Insights into strain-induced solid mesophases in melt-spun polymer fibers. Polymer 2021, 229, 124010. [Google Scholar] [CrossRef]
  35. Perret, E.; Reifler, F.A.; Gooneie, A.; Chen, K.; Selli, F.; Hufenus, R. Structural response of melt-spun poly(3-hydroxybutyrate) fibers to stress and temperature. Polymer 2020, 197, 122503. [Google Scholar] [CrossRef]
  36. Perret, E.; Reifler, F.A.; Gooneie, A.; Hufenus, R. Tensile study of melt-spun poly(3-hydroxybutyrate) P3HB fibers: Reversible transformation of a highly oriented phase. Polymer 2019, 180, 121668. [Google Scholar] [CrossRef]
  37. Perret, E.; Sharma, K.; Tritsch, S.; Hufenus, R. Reversible mesophase in stress-annealed poly(3-hydroxybutyrate) fibers: A synchrotron x-ray and polarized ATR-FTIR study. Polymer 2021, 231, 124141. [Google Scholar] [CrossRef]
  38. Schneider, K.; Zafeiropoulos, N.E.; Stamm, M. In situ Investigation of Structural Changes during Deformation and Fracture of Polymers by Synchrotron SAXS and WAXS. Adv. Eng. Mater. 2009, 11, 502–506. [Google Scholar] [CrossRef]
  39. Zaremba, D.; Evert, R. 5—Materials, chemical properties and analysis. In Polymer Optical Fibres; Bunge, C.-A., Gries, T., Beckers, M., Eds.; Woodhead Publishing: Cambridge, UK, 2017; pp. 153–186. [Google Scholar]
  40. Griffini, G. Host Matrix Materials for Luminescent Solar Concentrators: Recent Achievements and Forthcoming Challenges. Front. Mater. 2019, 6, 29. [Google Scholar] [CrossRef] [Green Version]
  41. Jakubowski, K.; Kerkemeyer, W.; Perret, E.; Heuberger, M.; Hufenus, R. Liquid-core polymer optical fibers for luminescent waveguide applications. Mater. Des. 2020, 196, 109131. [Google Scholar] [CrossRef]
  42. Quandt, B.M. Optical Fibre Textiles in Non-Invasive Medical Applications; ETH Zürich: Zurich, Switzerland, 2016. [Google Scholar]
  43. Kruhlak, R.J.; Kuzyk, M.G. Side-illumination fluorescence spectroscopy. I. Principles. J. Opt. Soc. Am. B 1999, 16, 1749–1755. [Google Scholar] [CrossRef]
  44. Kruhlak, R.J.; Kuzyk, M.G. Side-illumination fluorescence spectroscopy. II. Applications to squaraine-dye-doped polymer optical fibers. J. Opt. Soc. Am. B 1999, 16, 1756–1767. [Google Scholar] [CrossRef]
  45. Weiss, J.D. Trapping efficiency of fluorescent optical fibers. Opt. Eng. 2015, 54, 027101. [Google Scholar] [CrossRef] [Green Version]
  46. Itxaso, P.; María Asunción, I.; Joseba, Z.; Eneko, A.; Gaizka, D.; Nekane, G.; Olga, G.; Robert, E.; Daniel, Z.; Hans-Hermann, J.; et al. Polymer optical fibers doped with organic materials as luminescent solar concentrators. Proc.SPIE 2017, 10101, 102–109. [Google Scholar]
  47. Born, M.; Wolf, E. Electromagnetic theory of propagation, interference, and diffraction of light. In Principles of Optics, 7th (Expanded) ed.; Cambridge University Press: Cambridge, UK, 2019. [Google Scholar]
  48. Bunge, C.; Kruglov, R.; Poisel, H. Rayleigh and Mie scattering in polymer optical fibers. J. Lightwave Technol. 2006, 24, 3137–3146. [Google Scholar] [CrossRef]
  49. Yang, A.C.M.; Jou, E.D.Y.; Chang, Y.L.J.; Jou, J.H. The solvent-induced cracking in glassy polymer coatings by atomic force microscopy. Mater. Chem. Phys. 1995, 42, 220–224. [Google Scholar] [CrossRef] [Green Version]
  50. Selli, F.; Erdoğan, U.H.; Hufenus, R.; Perret, E. Mesophase in melt-spun poly(ɛ-caprolactone) filaments: Structure–mechanical property relationship. Polymer 2020, 206, 122870. [Google Scholar] [CrossRef]
  51. Stribeck, N. Analysis of SAXS Fiber Patterns by Means of Projections. In Scattering from Polymers; American Chemical Society: Washington, DC, USA, 1999; Volume 739, pp. 41–56. [Google Scholar]
  52. Guinier, A. X-ray Diffraction; W. H. Freeman: San Francisco, CA, USA, 1963. [Google Scholar]
  53. Sharma, K.; Braun, O.; Tritsch, S.; Muff, R.; Hufenus, R.; Perret, E. 2D Raman, ATR-FTIR, WAXD, SAXS and DSC data of PET mono- and PET/PA6 bicomponent filaments. Data Brief 2021, 38, 107416. [Google Scholar] [CrossRef]
  54. Gerasimov, V.I.; Genin, Y.V.; Tsvankin, D.Y. Small-angle X-Ray study of deformed bulk polyethylene. J. Polym. Sci. Part B-Polym. Phys. 1974, 12, 2035–2046. [Google Scholar] [CrossRef]
  55. Kumar, S.; Warner, S.; Grubb, D.T.; Adams, W.W. On the Small-Angle X-Ray-Scattering of Rigid-Rod Polymer Fibers. Polymer 1994, 35, 5408–5412. [Google Scholar] [CrossRef]
  56. Welch, B.L. The Significance of the Difference between Two Means when the Population Variances Are Unequal. Biometrika 1938, 29, 350–362. [Google Scholar] [CrossRef]
  57. Perret, E.; Braun, O.; Sharma, K.; Tritsch, S.; Muff, R.; Hufenus, R. High-resolution 2D Raman mapping of mono- and bicomponent filament cross-sections. Polymer 2021, 229, 124011. [Google Scholar] [CrossRef]
Polymers 14 03262 g001 550
Figure 1. Down-conversion of incoming light from side-illumination of a PL-POF into axially emitted red light. The PL dye (LR305) in the core of the PL-POF is responsible for the light conversion from blue to red. Reprinted/adapted image with permission from [15]. 2020, Elsevier.
Figure 1. Down-conversion of incoming light from side-illumination of a PL-POF into axially emitted red light. The PL dye (LR305) in the core of the PL-POF is responsible for the light conversion from blue to red. Reprinted/adapted image with permission from [15]. 2020, Elsevier.
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Figure 2. Schematic of pilot melt-spinning plant used to prepare PL-POFs.
Figure 2. Schematic of pilot melt-spinning plant used to prepare PL-POFs.
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Figure 3. Schematic representation of the setup used to measure the photoluminescence intensity at a defined distance, x, from the side-illumination point.
Figure 3. Schematic representation of the setup used to measure the photoluminescence intensity at a defined distance, x, from the side-illumination point.
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Figure 4. Microscopic cross-sections of core/sheath PL-POFs (DR = 1.1 and DR = 1.6) with doped COP core and pure THVP sheath.
Figure 4. Microscopic cross-sections of core/sheath PL-POFs (DR = 1.1 and DR = 1.6) with doped COP core and pure THVP sheath.
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Figure 5. Logarithmic plot of NSI-values and calculated sheath-related improvement parameters, Fsheath, for PL-POFs of DR = 1.1 and DR = 1.6. The fitting curves that are based on Equation (3) are shown as dashed curves.
Figure 5. Logarithmic plot of NSI-values and calculated sheath-related improvement parameters, Fsheath, for PL-POFs of DR = 1.1 and DR = 1.6. The fitting curves that are based on Equation (3) are shown as dashed curves.
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Figure 6. Schematic explanation of the effect of scattering in a semi-crystalline sheath onto axial light emission. The transversal transmission of light through a core/sheath PL-POF is shown in (a) and through a core-only fiber in (b). Corresponding longitudinal views are shown in (c,d). In summary, scattering in the sheath leads to prolonged optical pathways across the photoluminescent core, thus increasing the probability for light down-conversion with axial re-emission.
Figure 6. Schematic explanation of the effect of scattering in a semi-crystalline sheath onto axial light emission. The transversal transmission of light through a core/sheath PL-POF is shown in (a) and through a core-only fiber in (b). Corresponding longitudinal views are shown in (c,d). In summary, scattering in the sheath leads to prolonged optical pathways across the photoluminescent core, thus increasing the probability for light down-conversion with axial re-emission.
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Figure 7. WAXD and SAXS patterns for (a) PL-POF with DR = 1.1 and corresponding (b) core-only fiber. WAXD and SAXS patterns for (c) PL-POF with DR = 1.6 and corresponding (d) core-only fiber. The fiber axis is vertical.
Figure 7. WAXD and SAXS patterns for (a) PL-POF with DR = 1.1 and corresponding (b) core-only fiber. WAXD and SAXS patterns for (c) PL-POF with DR = 1.6 and corresponding (d) core-only fiber. The fiber axis is vertical.
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Figure 8. (a) Equatorial WAXD profiles and (b) azimuthal profiles of PL-POFs and corresponding core-only fibers. The inset in (a) shows the corrected equatorial intensity of the sheath material, which is obtained by subtracting the intensity of the core-only fiber from the PL-POF. The correction is explained in the main text. The intensity in the central region of (b), around ϕ = 0°, is slightly decreasing due to a polyimide foil that holds the beamstop.
Figure 8. (a) Equatorial WAXD profiles and (b) azimuthal profiles of PL-POFs and corresponding core-only fibers. The inset in (a) shows the corrected equatorial intensity of the sheath material, which is obtained by subtracting the intensity of the core-only fiber from the PL-POF. The correction is explained in the main text. The intensity in the central region of (b), around ϕ = 0°, is slightly decreasing due to a polyimide foil that holds the beamstop.
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Figure 9. Proposed structure of THVP sheath and COP core for (a) DR = 1.1 and for (b) DR = 1.6.
Figure 9. Proposed structure of THVP sheath and COP core for (a) DR = 1.1 and for (b) DR = 1.6.
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Table
Table 1. Production parameters of core/sheath PL-POFs.
Table 1. Production parameters of core/sheath PL-POFs.
Fiber Number Used at EmpaLabelGodet 1 Speed/
Temp.
(m/min, °C)		Godet 2 Speed/
Temp.
(m/min, °C)		Godet 3 Speed/
Temp.
(m/min, °C)		Godet 4 Speed/
Temp.
(m/min, °C)		Winder Speed
(m/min)		Draw
Ratio
1815Core/sheath 1.1140/54140/60147/30150/301481.1
1817Core/sheath 1.6140/54140/60223/30225/302231.6
Table
Table 2. Dimensions of PL-POFs.
Table 2. Dimensions of PL-POFs.
LabelCore Radius (µm) A c o r e
(mm2) 		Sheath Thickness (µm)Outer PL-POF Radius (µm)APL-POF (mm2)
Core/sheath, DR = 1.1144 ± 30.06521 ± 6165 ± 30.086
Core/sheath, DR = 1.6118 ± 40.04417 ± 7135 ± 30.057
Table
Table 3. Overview of measured and calculated optical parameters for core/sheath PL-POFs and core-only fibers with two different DRs. The error in the attenuation has been calculated using error propagation.
Table 3. Overview of measured and calculated optical parameters for core/sheath PL-POFs and core-only fibers with two different DRs. The error in the attenuation has been calculated using error propagation.
Fiberx
(cm)		Imeasured (x)
(pA)		 α
(dB/m) 		NSI(x)
(pA/mm2)
Core/sheath, DR = 1.110181 ± 1032.6 ± 42780 ± 146
15121 ± 61861 ± 98
2085 ± 81312 ± 117
Core-only, DR = 1.11049 ± 354.4 ± 11757 ± 48
1526 ± 4401 ± 58
2014 ± 3216 ± 53
Core/sheath, DR = 1.610126 ± 828.4 ± 42881 ± 178
1589 ± 62034 ± 134
2066 ± 51499 ± 117
Core-only, DR = 1.61030 ± 448.9 ± 13682 ± 89
1517 ± 3382 ± 73
2010 ± 3221 ± 59
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Perret, E.; Jakubowski, K.; Heuberger, M.; Hufenus, R. Effects of Nanoscale Morphology on Optical Properties of Photoluminescent Polymer Optical Fibers. Polymers 2022, 14, 3262. https://doi.org/10.3390/polym14163262

AMA Style

Perret E, Jakubowski K, Heuberger M, Hufenus R. Effects of Nanoscale Morphology on Optical Properties of Photoluminescent Polymer Optical Fibers. Polymers. 2022; 14(16):3262. https://doi.org/10.3390/polym14163262

Chicago/Turabian Style

Perret, Edith, Konrad Jakubowski, Manfred Heuberger, and Rudolf Hufenus. 2022. "Effects of Nanoscale Morphology on Optical Properties of Photoluminescent Polymer Optical Fibers" Polymers 14, no. 16: 3262. https://doi.org/10.3390/polym14163262

APA Style

Perret, E., Jakubowski, K., Heuberger, M., & Hufenus, R. (2022). Effects of Nanoscale Morphology on Optical Properties of Photoluminescent Polymer Optical Fibers. Polymers, 14(16), 3262. https://doi.org/10.3390/polym14163262

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