UU student #: 5582733 QUT student #: n9827102 Iris OTTO Dr.Phong TRAN Dr.Ir.Jos MALDA D/Prof.Dietmar W. HUTMACHER UMC – Utrecht University, Netherlands IHBI - Queensland University of Technology, Australia 01/09/2015 – 31/08/2017 SC80 Master of Applied Science MSc Biofabrication Final Thesis “Biofabrication: tools for new therapeutics in regenerative medicine and drug delivery. ” Submitted in fulfilment of the requirement for the degree of SC80 Master of Applied Science Science and Engineering Faculty Quentin Clément PEIFFER
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UU student #: 5582733
QUT student #: n9827102
Iris OTTO
Dr.Phong TRAN
Dr.Ir.Jos MALDA
D/Prof.Dietmar W. HUTMACHER
UMC – Utrecht University, Netherlands
IHBI - Queensland University of Technology, Australia
01/09/2015 – 31/08/2017
SC80 Master of Applied Science
MSc Biofabrication
Final Thesis
“Biofabrication: tools for new therapeutics in
regenerative medicine and drug delivery.” Submitted in fulfilment of the requirement for the degree of SC80 Master of Applied Science
Science and Engineering Faculty
Quentin Clément PEIFFER
P a g e 1 | 78
STATEMENT OF ORIGINAL AUTHORSHIP
The work contained in this thesis undertaken between QUT and Utrecht University has not
been previously submitted to meet requirements for an award at these or any other higher
education institution. To the best of my knowledge and belief, the thesis contains no material
previously published or written by another person except where due reference is made.
QUT Verified Signature
P a g e 2 | 78
FOREWORD
This Master thesis is the result of the collaboration between the Utrecht University (UU) and
the Queensland University of Technology (QUT). As such, this document is divided in two
independent section: the first part “Biofabrication of an auricular cartilage” is presenting the
work carried out at UU while the second part “ Microporous polycaprolactone scaffolds for drug
delivery” is presenting the work carried out at QUT. As such, each part features its own ab-
stract, keywords, abbreviation, acknowledgement, table of content and bibliography.
Biofabrication of an auricular cartilage………………………………p3 - 43
Microporous polycaprolactone scaffolds for drug delivery…………p44-78
P a g e 3 | 78
Biofabrication of an auricular
cartilage implant
Quentin Clément PEIFFER
UU student #: 5582733
MSc Biofabrication
Minor Research Project
RMC Utrecht
09/11/2015 – 10/06/2016
Daily supervisor: Dr.Phong Tran
Examiner: Dr.Ir.J.Malda
P a g e 4 | 78
LAYMAN’S SUMMARY
Facial malformations like ear loss due to cancer, burns, trauma or even birth defects can heav-
ily affect the relationship between an individual and their relatives or society. Current treat-
ments present severe drawbacks with highly variable aesthetic results. With the capacity to
combine different materials in a precise manner, 3D printers appeared in biomedical sciences
during the past few years as novel tools able to bring new solutions, such as scaffolds, that
can overcome all previous treatments. A scaffold in tissue engineering is a construct made of
a material compatible with the human body to repair damaged tissues. Yet, to provide these
new clinical solutions, 3D printers require considerable work for research and optimization. In
this work, the deposition of two materials is studied to combine them in an ear shape cartilage.
The first material is a thermoplastic that provides mechanical strength and consequently, the
printed scaffolds is not destroyed after grafting. The second material is a hydrogel; a hydrogel
is a gel able to absorb a high quantity of water and therefore, provides conditions for cells to
proliferate. To combine these two materials, it is first necessary to optimize the deposition of
each of them individually. The first part of this work is to study the potential of a new tool for
the deposition of the thermoplastic material. Since the printing process can kill the cells, the
second step of this work is to review the literature to predict how to deposit the hydrogel while
preserving the highest cell survival. The thermoplastic and hydrogel laden with cells were com-
bined in square constructs and analyzed in the third step of this work. The final phase of this
work focuses on the computer work related to the control of the printer, to assess which soft-
ware would be the most useful for carrying out the printing of two materials in an ear shape.
ABSTRACT
Microtia or ear loss are facial malformations for which no current treatments are perfectly
adapted. Additive manufacturing is a growing field and is expected to provide medical applica-
tions in the near future, especially by the creation of intricate scaffolds. This study explores the
co-manufacturing of hybrid PCL/gelMA scaffolds, specifically for ear cartilage engineering.
This research with a step-by-step approach aims to present the different challenges that
represent co-manufacturing and how they could be overcome. This includes a description of
Fused-deposition modeling (FDM) and Pressure-Assisted Bioprinting (PAB) with attention
given to the preservation of cell-viability. If the combination of FDM and PAB is not a technical
challenge, this work illustrates the importance of characterizing materials rheological proper-
ties to have control over the fabrication process. Therefore, after experimenting and backed
by literature, it appears that spraying cell with low inlet-pressure is the approach that preserves
the highest cell viability when dispensing a cell-laden hydrogel. At last, this work points out the
importance of considering the computer science behind additive manufacturing, and which
otherwise can rapidly become a limitation for tools capacities
REFERENCES [1] I. a Otto, F. P. W. Melchels, X. Zhao, M. a Randolph, M. Kon, C. C. Breugem, and J. Malda, “Auricular
reconstruction using biofabrication-based tissue engineering strategies,” Biofabrication, vol. 7, no. 3, p. 032001, 2015.
[2] W. Schuurman, V. Khristov, M. W. Pot, P. R. van Weeren, W. J. a Dhert, and J. Malda, “Bioprinting of hybrid tissue constructs with tailorable mechanical properties.,” Biofabrication, vol. 3, no. 2, p. 021001, 2011.
[3] Z. Izadifar, T. Chang, W. Kulyk, X. Chen, and B. F. Eames, “Analyzing Biological Performance of 3D-Printed, Cell-Impregnated Hybrid Constructs for Cartilage Tissue Engineering,” Tissue Eng. Part C Methods, vol. 22, no. 3, p. ten.tec.2015.0307, 2016.
[4] H.-W. Kang, S. J. Lee, I. K. Ko, C. Kengla, J. J. Yoo, and A. Atala, “A 3D bioprinting system to produce human-scale tissue constructs with structural integrity,” Nat. Biotechnol., vol. 34, no. 3, pp. 312–319, 2016.
[5] L. A. Bosworth, S. R. Rathbone, R. S. Bradley, and S. H. Cartmell, “Dynamic loading of electrospun yarns guides mesenchymal stem cells towards a tendon lineage,” J. Mech. Behav. Biomed. Mater., vol. 39, pp. 175–183, 2014.
[6] E. Díaz, I. Sandonis, and M. B. Valle, “In Vitro Degradation of Poly ( caprolactone )/ nHA Composites,” vol. 2014, 2014.
[7] W. J. Hendrikson, J. Rouwkema, C. a. van Blitterswijk, and L. Moroni, “Influence of PCL molecular weight on mesenchymal stromal cell differentiation,” R. Soc. Chem. Adv., vol. 5, no. 67, pp. 54510–54516, 2015.
[8] T. Billiet, E. Gevaert, T. De Schryver, M. Cornelissen, and P. Dubruel, “The 3D printing of gelatin methacrylamide cell-laden tissue-engineered constructs with high cell viability,” Biomaterials, vol. 35, no. 1, pp. 49–62, 2014.
[9] F. P. W. Melchels, W. J. a. Dhert, D. W. Hutmacher, and J. Malda, “Development and characterisation of a new bioink for additive tissue manufacturing,” J. Mater. Chem. B, vol. 2, no. 16, p. 2282, 2014.
[10] W. Schuurman, P. a. Levett, M. W. Pot, P. R. van Weeren, W. J. a Dhert, D. W. Hutmacher, F. P. W. Melchels, T. J. Klein, and J. Malda, “Gelatin-methacrylamide hydrogels as potential biomaterials for fabrication of tissue-engineered cartilage constructs,” Macromol. Biosci., vol. 13, no. 5, pp. 551–561, 2013.
[11] A. Faulkner-Jones, C. Fyfe, D.-J. Cornelissen, J. Gardner, J. King, A. Courtney, and W. Shu, “Bioprinting of human pluripotent stem cells and their directed differentiation into hepatocyte-like cells for the generation of mini-livers in 3D.,” Biofabrication, vol. 7, no. 4, p. 044102, 2015.
[12] K. Nair, M. Gandhi, S. Khalil, K. C. Yan, M. Marcolongo, K. Barbee, and W. Sun, “Characterization of cell viability during bioprinting processes,” Biotechnol. J., vol. 4, no. 8, pp. 1168–1177, 2009.
[13] K. C. Yan, K. Paluch, K. Nair, and W. Sun, “Effects of Process Parameters on Cell Damage in a 3d Cell Printing Process,” Imece2009 Proc. Asme Int. Mech. Eng. Congr. Expo. Vol 2, pp. 75–81\n525, 2010.
[14] M. Rimann, E. Bono, H. Annaheim, M. Bleisch, and U. Graf-Hausner, “Standardized 3D Bioprinting of Soft Tissue Models with Human Primary Cells.,” J. Lab. Autom., p. 2211068214567146–, 2015.
[15] H.-W. Kang, S. J. Lee, I. K. Ko, C. Kengla, J. J. Yoo, and A. Atala, “A 3D bioprinting system to produce human-scale tissue constructs with structural integrity,” Nat. Biotechnol., vol. 34, no. 3, pp. 312–319, 2016.
[16] Y. Yu, Y. Zhang, J. a Martin, and I. T. Ozbolat, “Evaluation of cell viability and functionality in vessel-like bioprintable cell-laden tubular channels.,” J. Biomech. Eng., vol. 135, no. 9, p. 91011, 2013.
[17] N. E. Fedorovich, M. H. Oudshoorn, D. van Geemen, W. E. Hennink, J. Alblas, and W. J. a Dhert, “The effect of photopolymerization on stem cells embedded in hydrogels,” Biomaterials, vol. 30, no. 3, pp. 344–353, 2009.
[18] J. Jung and J. Oh, “Influence of photo-initiator concentration on the viability of cells encapsulated in photo-crosslinked microgels fabricated by microfluidics,” Dig. J. Nanomater. Biostructures, vol. 9, no. 2, pp. 503–509, 2014.
[19] A. D. Rouillard, C. M. Berglund, J. Y. Lee, W. J. Polacheck, Y. Tsui, L. J. Bonassar, and B. J. Kirby, “Methods for photocrosslinking alginate hydrogel scaffolds with high cell viability.,” Tissue Eng. Part C. Methods, vol. 17, no. 2, pp. 173–179, 2011.
[20] J. Malda, J. Visser, F. P. Melchels, T. Jüngst, W. E. Hennink, W. J. a Dhert, J. Groll, and D. W. Hutmacher, “25th anniversary article: Engineering hydrogels for biofabrication,” Adv. Mater., vol. 25, no. 36, pp. 5011–5028, 2013.
Concerning the drug release, release solutions are pipetted in the tubes containing the scaf-
folds and placed in an orbital shaker incubator at 37°C (New Brunswick™ I26, Eppendorf).
Paclitaxel is released in 200µl of a PBS/Tween 20 0.1% mix due to its very poor solubility.
Cefazolin and Vancomycin are released in 200µl of PBS, and Dexamethasone is release in
2ml of PBS to avoid sink condition. The drug release is measured in UV-vis 96-well plates with
spectrophotometry similarly to the drug loss.
2.6 Normalization of drug release data
Three experimental repeats were done for each drug release study. Despite trying to be as
consistent as possible during each repeat, it appeared that the absolute quantity of drug re-
leased between experimental repeats can importantly vary depending on the drug. Those dif-
ferences between experimental repeats could be due to small variations of drug concentration
while preparing the stock solution for drug loading. But it is also possible that, for unknown
Fig 2. (a) Schematic representation of the loading process, (b) the drug loss measurement, (c)
drug release experiment and (d) the drug-scaffold bond characterization.
P a g e 56 | 78
reasons, the drug loading efficiency vary between experimental repeats. Hence, in absence of
precise control over the amount of drug released by the scaffolds no conclusions can be made
from the absolute value. Consequently, it was decided to focus on the release kinetics of each
drug rather than absolute values. To do so, data have been normalized by the overall quantity
of drug released.
2.7 Fourier Transform Infrared Spectroscopy (FTIR) analysis of paclitaxel-
loaded films
An FT-IR Spectroscopy analysis was performed to have a better understanding of the interac-
tion between paclitaxel and PCL. The FTIR analysis was carried out on both scaffolds and
films by nPCL and pPCL 44% with a Nicolet iS50 ATR-FTIR. Both scaffolds and films were
leached for 14 days in 0.01M NaOH before being loaded with paclitaxel, similarly to the drug
release experiments. The FTIR analysis was performed over the region 4000-400cm-1, each
spectrum is the average of 64 scans; results are presented in Fig. 6. The nPCL and pPCL
films used for the FTIR analysis were also observed with a stereomicroscope. Table 1 is based
on literature [58] [59] [60] and summarizes all the vibrational bands which could be potentially
associated with paclitaxel.
2.8 Cell culture
A primary cell line of human osteoblast (hOB) isolated from human's tibia bone were cultured
in flasks maintained in a humidified 5% CO2-containing atmosphere (37°C). The culture me-
dium was changed every 2 to 3 days and consisted of MEM-α with nucleotides and nucleosides
(Gibco, catalog number 12571), supplemented with 10% FBS, penicillin (100 U/mL), strepto-
mycin (100 μg/mL).
2.9 Dexamethasone bioactivity studies
Two cell experiments were carried out to determine the bioactivity of dexamethasone. The first
experiment was performed with free dexamethasone, while the second experiment used dex-
amethasone loaded scaffolds. In both experiment, 10^3 cells per well were seeded in 96 well
plate. In the first experiment, 24h after the cells were seeded, different doses of free dexame-
thasone were directly added to the culture media (from 260µg to 0.25µg). After 24 hours of
treatment, cell viability was assessed by Alamar blue and light microscopy pictures were taken.
In the second experiment, cell viability was assessed when exposed to pPCL 44w% and nPCL
scaffolds loaded with three doses of dexamethasone (150µg/scaffold; 30µg/scaffold; 6µg/scaf-
fold). Unlike drug release studies, the quantity of drug loaded is not normalized by the weight
of the scaffold, as it is important to have the same concentration of drug between samples.
P a g e 57 | 78
Cell viability was then measured by Alamar blue at D1, D3, and D5. Values measured with
Alamar blue were reported to an approximate cell number by using a standard curve.
3. RESULTS AND DISCUSSION
3.1 Rheology
Rheology is a powerful tool to study the viscoelastic behavior of a polymer. In this study, the
rheological analysis was carried out on the different composites to determine how the PBS
microparticles content affects the viscoelastic behavior of PCL. Bear in mind that G’’ and G’
respectively describes the viscous and elastic properties of a material. Tan (δ) corresponds
to the ratio of G’’ to G’, and as a result, depending on if tan (δ) tends to 0 or infinity, the closer
the samples resemble the properties of a pure solid or a pure fluid, respectively. In Fig. 3 & 4,
G’’ always has superior values than G’. This can be explained by the fact that measurements
are carried out at temperatures above the melting point of our polymers. Consequently, sam-
ples are melted and have viscous-dominant (liquid-like) properties, rather than elastic-domi-
nant (solid-like) properties, resulting in G’’ being superior to G’ and Tan (δ) being ≥1.
3.1.1 Amplitude sweep analysis: linear viscoelastic region of nPCL and pPCL
Amplitude sweep measurements were conducted to determine how the PBS microparticles
influence the linear viscoelastic region of neat PCL. Fig. 3 (a) & (b) respectively show the
storage modulus (G') and loss modulus (G") in function of the strain. Similarly to literature a
linear viscoelastic region (LVR) can be observed for neat PCL[61]. While this LVR is relatively
conserved for pPCL17%, this is not the case for PCL/Porogen 33% and 44%. The more the
content of PBS microparticles increases the less PCL shows linear viscoelastic properties. We
can also observe Fig. 3 & 4 that G’’ and G’ values increase with the amount of PCL micropar-
ticles. This trend has also already been observed in previous works with PCL/Silica nanocom-
posites [61]. However, G’ and G’’ are influenced differently depending on the amount of PBS
microparticles and the shear strain. Hence, it is more accurate to interpret the variations of G’’
and G’ together by plotting Tan (δ). First, we can see Fig. 3 (c) that tan (δ) is linear for neat
PCL, which means that G’’ and G’ stay relatively constant independently of the shear strain.
This linear behavior suggests that the internal friction of neat PCL is independent of the strain.
On the other hand, Tan (δ) loses its linear nature with higher content of porogen microparticles,
indicating that G’’ and G’ are influenced differently by the shear strain. Tan (δ) gets closer to 1
at low shear strain, meaning that G’ knows a bigger increase of its value relatively to G’’. Hence,
at low strain and at the same temperature, composites with higher PBS microparticles are
featuring more solid-like properties compared to neat PCL. And the fact that Tan (δ) increases
P a g e 58 | 78
Fig 3. Amplitude sweep tests results. G’, G’’ and Tan (δ) are respectively plotted in (a), (b) and (c) in function
of the shear strain (%) from 0.01% to 150%. Temperature was kept constant at 110°C and angular frequency
at 10 rad/sec. Each point is the average of three experimental repeats (N=3); the bars correspond to SD.
(a)
(c)
(b)
P a g e 59 | 78
with the shear strain, suggests that the properties of PCL/PBS composites get more and more
liquid-like as the strain increases until they finally reach the same state than neat PCL as the
structure starts to break down.
3.1.2 Temperature sweep analysis
In Fig. 4, G", G' and tan(δ) are plotted against the temperature from 125°C to 40°C, while shear
strain is kept constant at 1%. This analysis was carried out to determine how the PBS micro-
particles content influences G", G' or Tan (δ) depending on the temperature. When looking at
temperature sweep results, the first noticeable thing is that G’ and G’’ are linearly decreasing
with higher temperatures. These results can be rationalized by the fact that, as the temperature
gets higher the polymer get progressively closer and closer to a liquid-like state. Hence, vis-
cosity (G’’) and elasticity (G’) diminish as less force is required for the deformation of the ma-
terial. Similarly, to amplitude sweep results, G’ and G’’ have higher values as the amount of
PBS microparticles increases, yet again plotting Tan (δ) is necessary for further interpretation.
Thus, for a constant strain of 1% and between 55°C to 120°C Tan (δ) is lower for composites
with higher PBS microparticles content, which comparably to amplitude sweep results suggest
that those composites feature more solid-like properties. Interestingly, tan (δ) of PCL/PBS 33%
& 44% is linear and less steep than for neat PCL or PCL/PBS 17%, which on the other hand,
seem to be exponentials. These results suggest that neat PCL and PCL/PBS 17% viscoelastic
behaviors get exponentially close to a liquid as temperature rise. On the other hand, higher
PBS microparticles contents seem to make PCL less sensitive to temperature changes; and
at 110°C Tan (δ) of PCL/PBS 44% is almost twice lower than neat PCL. This result is compat-
ible with the fact that higher temperature is needed to print composites with higher microparti-
cles content. Finally, at low temperatures, a G' and G" crossover can be observed Fig. 4. (c).
This crossover means the material starts to behave like a viscoelastic solid and not like a melt
anymore. For this reason, measurements below 50°C are erratic because the material fully
cooled down and that the rheometer is unable to take a proper measurement. Interestingly,
the G'/G" crossover takes place between 55-50°C for the PCL/PBS 33% and 44%, while it
takes place between 50-45°C for neat PCL and PCL/PBS 17%. The temperature sweep anal-
ysis is achieved with decreasing temperatures as mentioned in material and methods. Thus, a
crossover point of G’/G’’ at a higher temperature would suggest that PCL cools down faster
with a high content of PBS microparticles. This behavior could be rationalized by the fact that
PBS microparticles reduce PCL particles freedom of movement which consequently cools
down faster.
P a g e 60 | 78
Fig 4. Temperature sweep results. G’, G’’ and Tan (δ) are respectively plotted in (a), (b) and (c) in
function of the temperature from 125°C to 35°C. Strain was kept constant at 1% and angular frequency
at 10 rad/sec. Each point is the average of three experimental repeats (N=3); the bars correspond to SD.
(c)
(b)
(a)
P a g e 61 | 78
3.2 Paclitaxel FTIR and Stereomicroscopy
The infrared spectrum of a compound is formed by the superposition of the absorption bands
of its specific functional groups and as such can be used as a fingerprint. Measurements were
first taken on porous paclitaxel-loaded scaffolds to be as close as possible of the experimental
conditions of the drug release experiment. However, results weren’t reproducible, which could
be linked to the architecture of scaffolds reducing the contact surface with the FTIR probe.
When using films rather than scaffolds, no paclitaxel signal could be detected on porous scaf-
folds either, even though the deposition of paclitaxel was confirmed by a drug loss measure-
ment (data not shown). We can see on stereomicroscope results Fig. 5 (c) & (d) that no dif-
ferences can be observed between the paclitaxel-loaded and the non-loaded porous film. On
the other hand, the deposition of paclitaxel is easily observable on non-porous film Fig. 5 (c)
& (d). This absence of a signal on porous films could be due to the paclitaxel being deposited
more homogeneously in the pores of the scaffold, resulting in a low drug signal on the surface
of the film. Paclitaxel signal was detectable on non-porous films only when the FTIR probe was
placed on the white drug clusters Fig. 5 (b). Consequently, the results presented are coming
from measurements taken on those white clusters of paclitaxel present on non-porous films.
The spectra presented in Fig 6. are discussed as follow. The spectra of PCL Fig. 6 (a) is
similar to literature [62] [63]. Thus, we can observe the peaks commonly identified such as the
methyl/methylene C-H saturated aliphatic groups asymmetric and symmetric stretching re-
spectively found at 2943 cm-1 and at 2864 cm-1. The strong absorption peak at 1720 cm-1 is
Fig 5. Stereomicroscopy pictures of non-porous (a) (b) films and porous (c) (d) films before (a) (c) and
after (b) (d) loading with paclitaxel. The red bars correspond to 1 mm.
(c)
(a) (b)
(d)
P a g e 62 | 78
assigned to the stretching vibration of the carbonyl compounds -C=O, and the signal at
1470.92 cm-1 seems to correspond to the bend of the methyl/methylene C-H saturated ali-
phatic. Finally, the signal at 1162 cm-1 and 730 cm-1 can be respectively assigned to the alkyl-
substituted ether -C-O-C- stretching and the rocking motion of the methylene. Fig. 6 (e) corre-
spond to the Paclitaxel spectra and is also comparable to what can be found in the literature
[59] [60]. Nonetheless, some bands can be attributed to different functional groups and differ-
ent interpretations were given. The wide vibrational band spreading from 3600cm-1 to 3200cm-
1 correspond to different functional groups such as the O-H hydroxyl stretching and the N-H
amine stretching. Some peaks in the 3130 cm-1 – 3070 cm-1 range could correspond to the C-
H aromatic stretching. Comparably to PCL, the two peaks at 2962 cm-1 – 2888 cm-1 are re-
spectively associated with the saturated aliphatic CH asymmetric and symmetric stretching
vibrations, while the peaks found at 1730 cm-1 and 1702 cm-1 are associated to the -C=O car-
bonyl groups (ester, ketone). The band at 1635 cm-1 is assigned to the amide C=O-N bound.
Literature has previously assigned the 1602 cm-1 band specifically to the aromatic C=C stretch-
ing vibration [60], but the next peaks at 1578 cm-1 and 1533 cm-1 are harder to identify and can
correspond to the amine N-H bends but also to the C=C-C aromatic stretching. The band at
1491 cm-1 is usually assigned to the bend of the methyl/methylene C-H saturated aliphatic
bend like for PCL. The signal at 1273 cm-1 has been previously attributed to the amine C-N
stretching [60] [59] and the strong band at 1241 cm-1 to the C-O ester bond stretching vibration
[60], which could be compatible with the peak found at 1251 cm-1 in the current work. Several
Table 1. Vibrational band assignments of Paclitaxel drug
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Figure 6. FTIR spectra of PCL (a) Paclitaxel (e) and non-porous PCL films loaded
with low dose (b) medium dose (c) and high dose (d) of paclitaxel
(a)
(b)
(c)
(d)
(e)
P a g e 64 | 78
functional groups can correspond to the band found at 1072 cm-1 and different interpretations
were given in the literature. Thus, it was assigned to the secondary alcohol C-O stretching [59]
or to the C-H out of plane deformation bands [60]. But the peak might be more likely to corre-
sponds to the secondary alcohol C-O stretching which can be assigned to a wide range of
absorption around 1150 cm-1 and 1000 cm-1 [58], while the C-H out of plane deformation
bands are assigned to the range of 900 – 670 cm-1 in general [58]. Nonetheless, it could cor-
respond to the C-H aromatic in-plane bend which is found in the range of 1225 cm1 to 950 cm-
1[58], and that can be assigned to several peaks, such as the band at 981 cm-1. Finally, the
band at 707 cm-1 and the surroundings ones are believed to correspond to the C-H aromatic
out of plane bend [58] [60], but could also possibly correspond to the O-H alcohol out-of-plane
bend[58] The peaks 707 cm-1/981 cm-1/1635 cm-1/1578 cm-1/1533 cm-1 will be specifically
kept as fingerprint of paclitaxel for our work. Fig 6. (b), (c) & (d) correspond to non-porous
PCL films respectively loaded with a low, medium, and a high dose of paclitaxel. The first thing
to notice is that no paclitaxel signal is detected for the low dose as the spectra is identical to
the one of PCL. On the other hand, we can clearly see that the bands associated with paclitaxel
and circled in red are becoming sharper as the dose increase. However, the bands visible in
Fig 6. (b), (c) & (d) are at the same positions than on the spectra of PCL and paclitaxel ob-
served separately. This absence of a shift is generally associated with an absence of
interaction between the two materials as no functional groups bonded between paclitaxel and
PCL.
3.3 Drug release
3.3.1 Porous and non-porous scaffolds
As mentioned in material and methods, all the scaffolds used for drug release experiments are
first leached for 14 days and then cut by hand with a scalpel to obtain small scaffolds of ap-
proximately 3mmx3mmx3mm. The quantity of drug loaded in each release study is normalized
Figure 7. Bar diagram representing the difference of weight between porous and non-
porous scaffolds of similar size after leaching. The bars correspond to SD (n=146)
P a g e 65 | 78
by the weight of each scaffold. For this reason, each scaffold is weight before the sterilization
and loading process. If more specific techniques are required to study the porosity of porous
scaffolds in details, we can already see Fig. 7 the significant difference in weight between
porous and non-porous scaffolds of the same size. Thus, porous scaffolds and non-porous
scaffolds respectively weight 5.6 mg and 9mg in average. Furthermore, it has been observed
during experimentation that porous scaffolds are floating in PBS
3.3.2 Drug loss and loading efficiency
The drug loss and loading efficiency were measured and calculated for all drug release exper-
iments as explained in material and methods. Unfortunately, the results can’t be shown as they
weren’t reproducible. It is not clear yet if the lack of reproducibility is simply due to variations
between experimental repeats or due to the experimental protocol. Thus, the experimental
protocol didn’t seem to work for cefazolin experiments. On the other hand, drug loss results
measured for vancomycin experiments seemed to match with the quantity of drug released by
the scaffolds. Yet again, the loading efficiency of vancomycin calculated for each experimental
repeat was very different. For dexamethasone, depending on the experiment repeat drug loss
results were either matching relatively well the drug release results or were incoherent. Finally,
paclitaxel drug loss results are explained in the next section.
3.3.3 Paclitaxel drug release
Fig. 8 corresponds to one of the three experimental repeats of the paclitaxel drug release
studies. This figure is here to draw attention to the amount of drug released by porous scaffolds
compared to non-porous scaffolds. If different amounts of paclitaxel were released depending
Figure 8. Paclitaxel cumulative release results normalised by the weight of scaffolds. High dose = 10
µg/mg scaffold. Medium dose = 2 µg/mg. Low dose = 0.4 µg/mg. The bars correspond to SD (N=1 / n=6)
P a g e 66 | 78
on the experimental repeat, porous scaffolds released significantly more drug than non-porous
scaffolds in all experimental repeats. When looking at the PCL films on Fig.5, we can observe
that the deposition of paclitaxel seems to be different on the porous and non-porous surface.
Thus, the deposition of paclitaxel on non-porous films is very heterogeneous as we can see
on Fig.5(b), therefore, this first result correlates with the idea that a bigger amount of paclitaxel
could be loaded on porous scaffolds, as observed on Fig.8, thanks to the surface porosity that
seems to allow a better paclitaxel deposition. Moreover, as paclitaxel is deposited in the scaf-
folds pores, the contact surface with the release medium is probably lower than on the non-
porous surface. This hypothesis would imply a faster release of paclitaxel for non-porous scaf-
folds onto which paclitaxel seems to form heterogeneous crystalline patches, yet, as explained
below, no real differences were found between the kinetics of porous and non-porous scaf-
folds. It is important to notice that only a very little amount of paclitaxel has been released
compared to the amount loaded. Fig. 8 we can notice that after 500 hours, porous scaffolds
loaded with high doses of paclitaxel (10µg/mg of scaffolds) released only 1.7µg/mg of the
scaffold, which is only equivalent to 17% of the initial amount of paclitaxel-loaded. Neverthe-
less, the amount of paclitaxel lost in the tube during loading for this experimental repeat was
corresponding to only 26% of the initial amount loaded in average. Suggesting that 57% of the
paclitaxel initially loaded is missing. The same phenomenon happened in the two other exper-
imental repeats. After sonication, a signal equivalent to 5% of the initial amount of paclitaxel-
loaded was measured for both porous and non-porous scaffolds, suggesting that a considera-
ble amount of paclitaxel could be potentially remaining on the surface of both porous and non-
scaffolds after 500 hours. The fact that a considerable amount of paclitaxel is not released
could be explained, either by an interaction between paclitaxel and PCL, or by paclitaxel being
too poorly soluble in PBS/tween 0.1%. If FTIR results aren’t sufficient to disprove entirely the
absence of interaction between PCL and Paclitaxel, it might be more likely that the release
medium is the source of the issue. When normalized by the total amount of drug released (Fig.
9), it is difficult to say if there is a difference between the release kinetics of porous and non-
porous scaffolds. It seems that porous scaffold loaded with a medium dose (Fig 9. b) could
have a very slightly slower release compared to non-porous scaffolds, but this difference is too
small to make any conclusion. Moreover, the results obtained for low dose and high dose are
not suggesting any differences between porous and non-porous scaffolds release (Fig 9. a,
c). The burst release is quite acceptable as after the first 24h only 20% to 30% of the drug is
released. Paclitaxel is then released over the course of approximately 20 days, which is a
significant amount of time, but we can see that after 200 hours the paclitaxel release signifi-
cantly slow down as 80% of the drug content has been released. The fact that release experi-
ments were stopped after 500h for practical reasons also need to be taken into account as a
P a g e 67 | 78
Figure 9. Paclitaxel cumulative release results normalised by the total amount of drug released.
High dose = 10 µg/mg scaffold. Medium dose = 2 µg/mg. Low dose = 0.4 µg/mg. Each point is the
average of 6 replicates (N=3).
(a)
(b)
(c)
P a g e 68 | 78
small amount of paclitaxel was still being released, especially for samples loaded with high
doses. Therefore, technically the release of paclitaxel lasts longer than 500 hours.
3.3.3 Dexamethasone: drug release
When normalized by the total amount of dexamethasone released (Fig 10.), no differences
can be observed in the release kinetic between porous and non-porous scaffolds. Unlike
paclitaxel, the burst release in the first 24h is more important and seems to be dose dependent.
Therefore, after 24h scaffolds loaded with a low dose of dexamethasone released 30% to 65%
of their dexamethasone, while scaffolds loaded with a high dose released 70% to 75%. There-
fore, it seems that the burst release of dexamethasone in the first 24h gets more important as
the dose loaded on the scaffold increase. Finally, most of the dexamethasone is getting re-
leased over the first 4 days. Thus, scaffolds loaded with a low dose of dexamethasone released
80% of their content, while scaffolds loaded with a high dose released 95% of
3.3.4 Dexamethasone: bioactivity
The cell viability of hOB exposed to different doses of free dexamethasone for 24h is presented
in Fig 11. A clear drop in cell viability can be observed between 325 µg/ml and 650 µg/ml of
dexamethasone, statistical analysis revealed that this drop is statistically significant. The mi-
croscopy pictures (data not shown) also shown that in addition to having fewer cells, a signifi-
cant amount have a round morphology when exposed to high dose of dexamethasone. Below
325 µg/ml and above 2.5 µg/ml of dexamethasone, it is difficult to make assumptions about
any effect of dexamethasone, as cell viability remain relatively similar to the cell control. No
differences can be observed either on the light microscopy pictures below 325 µg/ml. The
concentration of 2.5 µg/ml 1 .3 µg/ml seems to slightly increase the cell viability, but no statis-
tically significant differences were found. However, literature tends to suggest that dexame-
thasone is still toxic at a concentration of 1.3 µg/ml[64], consequently, no conclusion can be
made. Fig 12. we can see the cell viability of hOB while exposed to porous and non-porous
scaffolds loaded with three doses of dexamethasone (150µg/scaffold, 30 µg/scaffold, 6
µg/scaffold) over 5 days. After 24h of treatment, it appears that hOB cultured with scaffolds
loaded with high doses of dexamethasone have statistically significantly lower cell viabilities,
while the other conditions are comparable to controls. At day 3, the cell viability of hOB cultured
with dexamethasone-loaded scaffolds have increased compared to day 1 and are statistically
significantly higher than the controls. Interestingly, if no differences were found for porous scaf-
folds; the non-porous scaffolds loaded with a medium and low dose of dexamethasone have
a significantly higher cell viability than the one loaded with a high dose. On the other hand, cell
viability of the controls is lower than at day 1. At day 5, the cell viability of hOB cultured with
P a g e 69 | 78
Figure 10. Dexamethasone cumulative release results normalised by the total amount of drug
released. High dose = 25 µg/mg scaffold. Medium dose = 5 µg/mg. Low dose = 1 µg/mg. Each
point is the average of 6 replicates (N=3).
(a)
(b)
(c)
P a g e 70 | 78
loaded scaffolds is lower than at day 3 but remain higher than at day 1. The control conditions
have similar cell viability than at day 3 and remain statistically significantly lower than scaffolds
loaded with dexamethasone. It is interesting to notice that the standard error means of control
conditions are considerable comparably to other conditions. Compared to day 3, non-porous
scaffolds loaded with medium and low doses-maintained similar cell viabilities, while other
conditions seem to have slightly lower values. Moreover, non-porous scaffolds loaded with
medium and low doses have a statistically significantly higher cell viability than for high doses;
again, no differences were found for porous scaffolds. Consequently, the cytotoxicity associ-
ated with the high dose of dexamethasone suggest the dexamethasone released from the
scaffold is still bioactive. Passed day 1, results suggest that scaffolds loaded with dexame-
thasone increase cell viability similarly to the previous assay. Moreover, for unknown reasons,
Figure 11. Human osteoblasts cell viability assay measured by alamar blue after incubation of
24h with free dexamethasone. Bars correspond to SEM (N=1; n=8). A T-test analysis was car-
ried out to verify the statistical difference of the mean values (**=p < 0.01).
**
**
Figure 12. Human osteoblasts cell viability assay measured by alamar blue at day 1, 3 and 5 when
exposed to scaffolds loaded with dexamethasone (High dose = 150µg/scaffold; Medium =
30µg/scaffold; Low dose = 6µg/scaffold). Bars correspond to SEM (N=3; n=4) A one-way analysis
of variance was carried out to verify the statistical difference of the mean values (**=p < 0.01).
P a g e 71 | 78
Figure 13. Cefazolin cumulative release results normalised by the total amount of drug released.
High dose = 10 µg/mg scaffold. Medium dose = 2 µg/mg. Low dose = 0.4 µg/mg. Each point is the
average of 6 replicates (N=2).
(a)
(b)
(c)
P a g e 72 | 78
this phenomenon seems to be more important for cell exposed to low dose of dexamethasone
on non-porous scaffolds. Yet again literature has shown a decrease of cell viability and an
increase of cell apoptosis of hOB when exposed to a concentration of 10-6M [64]. Thus, it is
difficult to draw a conclusion on the ability of dexamethasone to increase cell viability. One
possible explanation could be that, passed the burst release of day 1, very small amount of
dexamethasone below the concentration of 10-6M are released which then stimulate cell
growth. Finally, it can be noticed that the NaOH leaching process applied to porous and non-
porous scaffolds doesn’t seem to have a negative impact on cell viability, as no statistically
significant differences could be found among the controls.
3.3.5 Cefazolin drug release
Unlike paclitaxel and dexamethasone, when looking at the normalized results Fig 13. we can
clearly see a different release kinetic between porous and non-porous scaffolds. Thus, porous
scaffolds release cefazolin more gradually over more than 100h, while non-porous scaffolds
release all the cefazolin in a burst during the first three hours. Like for dexamethasone, the
burst release of porous scaffolds in the first three hours seems to increase with the dose of
cefazolin. We can also observe that for both porous and non-porous scaffolds, cefazolin seems
to be released faster as the dose increases. Consequently, after 24h, low dose porous and
non-porous scaffolds respectively released 68% and 89% while high dose porous and non-
porous scaffolds respectively released 85% and 99% of the total amount of cefazolin. For un-
known reasons, the experimental protocol to measure drug loss is not working for cefazolin,
and very small values of drug loss are obtained while a significant drug loss is expected as
only 40% of the cefazolin initially loaded was released on average. Finally, those first results
are promising as porous scaffolds seem to be able to release cefazolin over a longer span of
time. However, it is important to take into account the fact that the burst effect and release
kinetics get respectively higher and faster as the dose of cefazolin increases. Consequently, it
could be interesting to see if the difference of release kinetic between porous and non-porous
scaffolds still exist at higher doses.
3.3.6 Vancomycin drug release
We can see Fig 14. results of the vancomycin release experiments normalized by the total
amount of vancomycin released. Even though the difference is not as considerable as the one
observed previously for cefazolin, porous scaffolds are clearly releasing vancomycin slightly
slower than non-porous scaffolds. Interestingly, this difference is hardly visible for low dose
samples. Results of low dose samples are often more spread as the measured values are very
small compared to high doses and are more influenced by measurement variation and errors
P a g e 73 | 78
Figure 14. Vancomycin cumulative release results normalised by the total amount of drug re-
leased. High dose = 10 µg/mg scaffold. Medium dose = 2 µg/mg. Low dose = 0.4 µg/mg. Each
point is the average of 6 replicates (N=3).
(a)
(b)
(c)
P a g e 74 | 78
as such. Unfortunately, the burst release of vancomycin is way more important than for
cefazolin, and most of the vancomycin present on the scaffold surface is released in PBS in
the first three hours for both type of scaffold. It is interesting to notice that similarly to cefazolin
and dexamethasone results, the burst release of vancomycin increases with the dose inde-
pendently of the scaffold type. Therefore, 87% of the vancomycin is released by porous scaf-
fold loaded with high dose in the first hour, while porous scaffold loaded with a low dose re-
leased only 67% of the vancomycin.
3.3.7 Final discussion
To get more insight into the factors influencing the drug release studies, it is important to dis-
cuss the results all together besides analyzing them separately. One main question arises from
this work; why the release kinetics is different between porous and non-porous scaffolds only
for cefazolin and vancomycin? In an attempt to explain the results, it is logical to look first at
the properties of the drug. Cefazolin and vancomycin have in common a high solubility in water,
on contrary to paclitaxel and dexamethasone which both have a very poor solubility in water.
This difference of solubility in water is the first element of the answer, even if it doesn’t explain
by itself how it influences the release kinetics of the drug between a porous and non-porous
scaffold. As mentioned earlier for Paclitaxel, it would be interesting to investigate if a different
release kinetics is observed with a release media in which paclitaxel and dexamethasone are
more soluble. Secondly, it appeared during experimentation that both porous and non-porous
scaffolds are sinking when placed in ethanol during drug loading. Yet, non-porous scaffolds
sink while porous scaffolds float when immersed in PBS or in cell media. This phenomenon
could be explained by the lower surface tension of ethanol combined with the hydrophobicity
of PCL. Thus, small air bubbles could be entrapped in the micropores of porous scaffolds,
making the scaffolds float in PBS but sink in liquid with lower surface tension such as ethanol.
The presence of air bubbles on the scaffold surface could also reduce the surface contact
between the release medium and the scaffold, which as a result would reduce the amount of
drug released. Hence, drug release results might be different if porous scaffolds were fully
immersed in the release media. Further experimentations could also help us have a better
understanding of what’s happening. Therefore, it would be important to extend the FTIR anal-
ysis to cefazolin, vancomycin, and dexamethasone as the difference between the results could
also due to a possible interaction between the drug and the scaffold. Indeed, depending on the
type of bonding created between the drug and the scaffold after loading, the release of the
drug could be hindered if immersion in the release media is not sufficient to detach the drug
from the scaffold. Moreover, it could also be interesting to analyze the homogeneity of each
drug deposition on the surface of porous and non-porous scaffolds as the release will directly
depend on the way each drug adheres to the surface. It was clear from Fig.5 that deposition
P a g e 75 | 78
of paclitaxel on non-porous films was not heterogeneous while no conclusion could be made
for the porous film as the limitations of light microscopy, notably the light reflection of PCL,
don’t allow us to visualize drug deposition in the scaffold pores. However, more advanced
imaging technologies such as scanning electronic microscopy might make possible the obser-
vation of the drug deposition in the pores.
4. CONCLUSION AND FUTURE WORK
First, this work investigated the printability of a novel PCL/PBS composite. Rheological meas-
urements have shown that as the mass ratio of PBS microparticles increase PCL is losing its
linear viscoelastic region, in addition, to being less sensitive to temperature increase. The
PCL/PBS composite was then successfully printed into scaffolds with a screw-based extrusion
3D printing technique by increasing the manufacturing temperature. Secondly, this work inves-
tigated the potential of PCL scaffolds as a drug carrier, and more precisely how the scaffold
microporosity is influencing the release kinetics of different drugs. Our results have shown that
porosity seems to decrease the burst effect and prolong the drug release of soluble drugs
compared to non-porous scaffolds. On the other hand, no significant differences could be ob-
served for scaffolds loaded with insoluble drugs. But despite some encouraging results, the
burst release remains important for soluble drugs, and as such, their clinical relevance remains
limited. Concerning the influence of the loading process, results seem to indicate that it is not
affecting the drug bioactivity since a high concentration of dexamethasone has shown a nox-
ious effect on cell viability. Obviously, further work is required to verify the drug bioactivity of
Paclitaxel, cefazolin, and vancomycin. Finally, results of drug release studies have also shown
a lack of control over the drug loading process. Indeed, the total amount of drug released
between experimental repeats was considerably different. As such, there is a strong need to
find an assay that would allow us to measure accurately the drug loss during the loading pro-
cess. Without this data, it is difficult to draw a conclusion as we’re unable to know precisely
how much drug has been released comparatively to the total amount loaded on each scaffold,
which would maybe show different release kinetics. To follow up this work two experiments
could be carried out to shed more light on the results. Firstly, HPLC could maybe be used to
measure the amount of drug left in the tube after loading; secondly, the scaffolds could maybe
be degraded in a solution which doesn’t affect the drug to measure how much drug is left on
the scaffolds at the end of the drug release study. Thus, more work is required to determine if
experimental conditions are optimal to get more insight into how porosity exactly affects drug
loading and drug release.
P a g e 76 | 78
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