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Bionic Nanosystems
Manu Sebastian Mannoor
A DISSERTATION
PRESENTED TO THE FACULTY
OF PRINCETON UNIVERSITY
IN CANDIDACY FOR THE DEGREE OF
DOCTOR OF PHILOSOPHY
RECOMMENDED FOR ACCEPTANCE
BY THE DEPARTMENT OF
MECHANICAL AND AEROSPACE ENGINEERING
ADVISER: MICHAEL C. MCALPINE
JUNE 2014
© Copyright by Manu Sebastian Mannoor, 2014.
All rights reserved.
iii
Dedication
To my loving wife Teena, for all her encouragement, forbearance, prayers and support.
*****
To Amma, for all her sacrifices and prayers.
*****
To God almighty - my help and refuge.
Great are the works of the LORD, studied by all who delight in them. (Psalm 111:2)
iv
Abstract
Direct multidimensional integration of functional electronics and mechanical elements with
viable biological systems could allow for the creation of bionic systems and devices possessing
unique and advanced capabilities. For example, the ability to three dimensionally integrate
functional electronic and mechanical components with biological cells and tissue could enable
the creation of bionic systems that can have tremendous impact in regenerative medicine,
prosthetics, and human-machine interfaces. However, as a consequence of the inherent
dichotomy in material properties and limitations of conventional fabrication methods, the
attainment of truly seamless integration of electronic and/or mechanical components with
biological systems has been challenging.
Nanomaterials engineering offers a general route for overcoming these dichotomies,
primarily due to the existence of a dimensional compatibility between fundamental biological
functional units and abiotic nanomaterial building blocks. One area of compelling interest for
bionic systems is in the field of biomedical sensing, where the direct interfacing of nanosensors
onto biological tissue or the human body could stimulate exciting opportunities such as on-body
health quality monitoring and adaptive threat detection. Further, interfacing of antimicrobial
peptide based bioselective probes onto the bionic nanosensors could offer abilities to detect
pathogenic bacteria with bio-inspired selectivity. Most compellingly, when paired with additive
manufacturing techniques such as 3D printing, these characteristics enable three dimensional
integration and merging of a variety of functional materials including electronic, structural and
biomaterials with viable biological cells, in the precise anatomic geometries of human organs, to
form three dimensionally integrated, multi-functional bionic hybrids and cyborg devices with
unique capabilities.
v
In this thesis, we illustrate these approaches using three representative bionic systems: 1)
Bionic Nanosensors: featuring bio-integrated graphene nanosensors for ubiquitous sensing, 2)
Bionic Organs: featuring 3D printed bionic ears with three dimensionally integrated electronics
and 3) Bionic Leaves: describing ongoing work in the direction of the creation of a bionic leaf
enabled by the integration of plant derived photosynthetic functional units with electronic
materials and components into a leaf-shaped hierarchical structure for harvesting photosynthetic
bioelectricity.
vi
Acknowledgements
This journey of the past 5 years in graduate school would not have been a success without the
generous help, guidance, support and prayers of many truly incredible and amazing people.
First and foremost, I would like to express my deepest gratitude to my advisor Professor
Michael McAlpine. He is an amazing scientist and mentor and his guidance encouragement and
support had the greatest influence on my success as a graduate student. His mentoring style that
is custom to each one of his lab members, paying attention to their specific strengths and
weaknesses is admirable. He pushed me to develop my weaknesses and exploit my strengths. I
cannot thank him enough for showing confidence in me and offering continued support for in all
my scientific endeavors. Further, I am extremely grateful of his patience to withstand my many
failures and stupid mistakes that I made along the way of my graduate career. He patiently
corrected me in the right direction without ever taking offenses at my mistakes. From the
beginning of my Ph.D. research, Professor McAlpine was keen in training me to be an
independent researcher-by encouraging me to come up with new and cutting-edge research ideas
and guiding me in this process of developing these ideas and gathering rigorous scientific results
by asking the key questions. His hard work and commitment has always been an inspiration for
me. Further, over the years, he trained me in writing high impact publications as well as in
maintaining highest standards in published results. Progressively towards the end of my graduate
studies, he started giving more weightage to develop my ability to do independent research and
thereby preparing me to start a career in academia (which Professor McAlpine always
encouraged each one of us to pursue). In addition, having had the opportunities to serve as
Assistant in Instruction with him, being a true and passionate teacher himself, he has given me
tips and advices many times in improving my teaching skills. All of these I believe to be a very
vii
unique and most valuable experience for any Ph.D. student. I am very thankful to him for this
training and feel myself to be very lucky to have had his guidance and the chance to work under
his supervision as a Ph.D. student.
Next, I would like to thank the past and current members of the McAlpine lab, whose
help and support many times has been instrumental in the success of my research projects. I
would like to especially thank Dr. Yi Qi, Dr. Yue Cui, Ann Mularz, Dr. Thanh Nguyen, Dr.
Kellye Cung, Yao-Wen Yeh, Dr. Maneesh Gupta, Dr. Blake Johnson, Huai-An Chin, Ian
Tamargo, Nina Masters and all the undergraduate researchers over the years for their help and
keeping me company in the lab. I would also like to thank in a very special way, Yong Lin Kong,
my good friend inside and outside the lab for his company and willingness to help always. I
would also like to thank Ziwen Jiang, a high school researcher from Peddie School (soon to be
an undergraduate student at MIT) and Jeff Clayton, a former Chemistry senior thesis student
(now graduate student at MIT) with whom I had the privilege to work on some incredible
projects.
I would like to thank my collaborators and those who served as academic and research
mentors all throughout my graduate career. I do not have words to adequately express my
genuine appreciation and gratitude to them, who were so generous in providing me guidance and
support along way of my graduate studies. I am very much indebted to Professor Claire Gmachl,
Professor of EE and vice dean of SEAS, for being always willing to give me advice and guidance
and for her continued support through the entire 5 years of my graduate life in Princeton. I also
want to express my deepest gratitude to Professor Winston Soboyejo of MAE for his advice,
guidance and continued support all throughout my Ph.D. years. I do not have words to express
my gratitude and respect to Professor Barrie Royce, Professor Emeritus in MAE, for his
viii
continued guidance, support and also for his generous help with the preparation for Ph.D. general
exam. I also do not know how to even begin to thank Dr. Nan Yao, director of PRISM imaging
and Analysis center for being so generous and a great teacher and teaching me everything that I
know of materials characterization and imaging- I benefitted immensely from his materials
characterization class MSE 505. I also wish to extend my appreciation and gratitude to Professor
David Gracias of Johns Hopkins University, for collaboration and valuable suggestions in the 3D
Printed Bionic Ear project and also for his support, Professor Naveen Verma of EE for the
collaboration in both the bionic nanosensor and bionic ear project and also for help with
electrical measurements for always being so willing to help when I show up at his office and
Professor James Link for collaboration in the antimicrobial peptide characterization project. I
don’t have words to adequately convey my appreciation and gratitude to Dr. Roger Cubicciotti,
President Nanomedica Inc., Professor Howard Stone of MAE, Professor Thomas Thundat of
University of Alberta, Professor George John of CUNY, Professor Marc Madou of UC Irvine,
Dr. Bill Braunlin and Dr. Les Beadling of RAD for their advice and continued support. Also, I
want to thank other faculty members in MAE: Professor Mikko Haataja, director of graduate
studies, Professor Craig Arnold, Professor Philip Holmes and everybody else who were generous
in helping me in my graduate life at Princeton. I also want to thank my Master’s advisor Dr.
Dentcho Ivanov for his guidance and support during the years of my Masters in Biomedical
Engineering at NJIT. I thank Professor Fiorenzo Omenetto of Tufts University, Professor
Amartya Sengupta of IIT Delhi (previously at Geoscience Department, Princeton) for
collaboration and valuable discussion in the bionic nanosensor project. My special thanks go to
Dr. Karen Malatesta of MAE for training me in cell culture and related protocols and for good
conversations and keeping company in the biolab. Also, one of the most beautiful part of
ix
graduate school was going through it together with other graduate students. I want to thank all
my friends whom I met in Princeton- Anand Ashok, Fadi Abdeljawad, Srevatsan Muralidharan,
Stimit Shah, Bryan Benson, Josh Heyne, Ismail Yakub, Yusuf Oni, Mykola Bordyuh and others
who made the Ph.D. years fun and wonderful!
I also couldn’t have done without the help of administrative staff members of MAE,
PRISM MFNL and IAC. Thanks very much to Jill Ray, our graduate administrator for all her
help and encouragement for academic and life matters. Also, thanks to Candy Reed, Carolyn
Arnesen, Joe Palmer, Dr. Pat Watson, Jerry Poirier for all the help and assistance. My thanks
also goes to Jonathan Prevost for all this help, support and good conversations and Mike
Vocaturo for all this help during last 5 years.
I also want to thank Father Dave Swantek and Father Martin Miller, chaplains at
Princeton University for their prayers and personal guidance. My deepest gratitude also goes to
Saint John’s soup kitchen, Newark, NJ and our friends and family for their constant prayers,
generous support all throughout.
Finally, I would like to thank my beautiful wife Teena and our wonderful son John.
Teena’s encouragement, constant prayers, quiet patience and unwavering love were undeniably
the driving force and inspiration for the past several years of my life. The sacrifices that she took
and her tolerance is a testament in itself of her patient love and unyielding support. Being a
graduate student herself at Johns Hopkins University, doing Ph.D. in a closely related field, I feel
so blessed to have taken this journey of graduate school with her company. Although, our
evenings and weekends were often filled with conversations about failed experiments or rejected
manuscripts, seeing the cutest smile on my son’s face (which he seem to reserve for the most
x
desperate moments in our life) makes us forget all the aches and pains of the day and divert my
attention to yet more subtle but joyous things in my life. I would also like to thank my mother,
brothers and sister, Teena’s parents and brother and sisters for their continued prayers and
encouragement.
Most of all, I am grateful to the Lord for watching over all my steps and guiding me in
my paths. “From whence cometh my help? My help cometh from the Lord, who made heaven
and earth” ( Psalm 121:1-2)
This dissertation carries T-3282 in the records of the Department of Mechanical and Aerospace
Engineering.
xi
Table of Contents
Dedication ...................................................................................................................................... iii
Abstract .......................................................................................................................................... iv
Ackowledgements .......................................................................................................................... vi
Table of Contents ........................................................................................................................... xi
List of Figures ............................................................................................................................. xvii
Chapter 1 ........................................................................................................................................1
Bionic Systems: Introduction ........................................................................................................1
1.1 Bionics ..............................................................................................................................1
1.2 History of Bionics:Implantable Devices and Prosthetics..................................................2
1.3 Biological Materials and Systems .....................................................................................5
1.4 Disparity in Properties between Engineered Systems and Biological Systems ................7
1.4.1 Dichotomy in Formation .............................................................................................8
1.4.2 Limitations of the Current Fabrication Methods ........................................................9
1.5 Overcoming the Differences: Nanoscale Science and Engineering ..............................10
1.5.1 Nanoscale Mechanics: Influence of Size on Mechanical Behavior ..........................11
1.6 Nanoscale Functional Electronic and Structural Materials ............................................12
1.6.1 Carbon Nanomaterials and Graphene ......................................................................13
1.6.2 Semiconducting Quantum Dots ...............................................................................16
1.6.3 Metallic Nanoparticles, Nanowires and Nanorods ..................................................17
xii
1.7 Bioorthogonal Approaches for Bionic Integration .........................................................18
1.7.1 Biomimetics: Engineering biocompatibility via biomimicry ..................................18
1.7.2 Self- Assembly ........................................................................................................19
1.7.3 Phage display ...........................................................................................................20
1.7.4 Tissue Engineering ..................................................................................................21
1.8 Additive Manufacturing for Bottom-up Three Dimensional Integration .......................22
1.9 Thesis Overview .............................................................................................................23
1.10 References .....................................................................................................................24
Chapter 2 ......................................................................................................................................35
Bionic Nanosensors ......................................................................................................................35
2.1 Overview .........................................................................................................................35
2.2 Biointegration of Sensors ................................................................................................35
2.3 Results & Discussion ....................................................................................…………..38
2.3.1 Graphene Silk Sensor ................................................................................................38
2.3.2 Materials Integration and Characterization ...............................................................40
2.3.3 Functionalization of graphene with AMPs ...............................................................48
2.3.4 Single bacterium detection ........................................................................................51
2.3.5 Wireless remote query monitoring of S.aureus. .......................................................54
2.3.6 Tooth platform monitoring of breath and saliva .......................................................57
2.3.7 Discussion .................................................................................................................60
xiii
2.4 Materials & Methods ......................................................................................................62
2.4.1 Reagents and Biologicals ..........................................................................................62
2.4.2 Prepartion of silk films.............................................................................................62
2.4.3 Fabrication of Graphene/silk sensors ........................................................................63
2.4.4 Biotransfer onto biomaterials ....................................................................................63
2.4.5 Graphene functionalization with AMPs ....................................................................63
2.4.6 Single bacterium detection measurements ................................................................64
2.4.7 Wireless sensing experiments ...................................................................................65
2.5 Conclusion ......................................................................................................................70
2.6 References .......................................................................................................................71
Chapter 3 ......................................................................................................................................79
Antimicrobial Peptides as Molecular Probes on Bionic Sensors ................................................... 79
3.1 Overview .........................................................................................................................79
3.2 Introduction .....................................................................................................................80
3.3 Antimicrobial Peptide based Sensitive Detection of Bacteria ........................................83
3.4 Effect of AMP Immobilization Density ..........................................................................87
3.5 Selectivity Measurements ...............................................................................................89
3.6 Real-Time Detection .......................................................................................................95
3.7 Materials and Methods ....................................................................................................97
3.7.1 Antimicrobial Peptides and Bacterial Cells ..............................................................97
xiv
3.7.2 Interdigitated Microelectrode Array (IMA) and Microfluidic Flow Cell .................98
3.7.3 Sensor Surface Functionalization with Magainin .....................................................99
3.7.4 Fluorescent Microscopy ............................................................................................99
3.8 Impedance Spectroscopy Measurement Details ...........................................................100
3.8.1 Measurement setup .................................................................................................101
3.8.2 Equivalent Circuit ...................................................................................................102
3.9 Conclusion ....................................................................................................................104
3.10 References ...................................................................................................................105
Chapter 4 ....................................................................................................................................112
3D Printed Bionic Ears .................................................................................................................. 112
4.1 Overview .......................................................................................................................112
4.2 Introduction ...................................................................................................................112
4.3 Our Approach................................................................................................................114
4.4 3D Printing of Bionic Ear: Steps ..................................................................................115
4.5 Growth and Viability of the Bionic Ear ........................................................................117
4.5.1 Viability of the Printing Process .............................................................................119
4.6 Histologic Characterization ..........................................................................................120
4.7 Biochemical and Biomechanical Characterization .......................................................121
4.7.1 Tensile Testing 3D Printed Cartilage Dog bones ...................................................122
4.7.2 Hardness Testing of 3D Printed Neocartillage .......................................................123
xv
4.8 Electrical Characterization ............................................................................................123
4.8.1 Bionic Ears: Listening of Stereo Music ..................................................................126
4.9 Materials and Methods ..................................................................................................126
4.9.1 Chondrocyte Culturing............................................................................................126
4.9.2 Alginate Formulation and Chondrocyte Seeding ....................................................127
4.9.3 3D Printing ..............................................................................................................127
4.9.4 Culturing conditions...............................................................................................128
4.9.5 Cellular and Tissue Viability ..................................................................................131
4.9.6 Biochemical Analyses .............................................................................................132
4.9.7 Histologic Evaluation of the Bionic Ear .................................................................136
4.9.8 Biomechanical Characterization .............................................................................138
4.10 Conclusions .................................................................................................................141
4.11 References ...................................................................................................................142
Chapter 5 ....................................................................................................................................147
3D Printed Bionic Leaves for Photosynthetic Bioelectricity .................................................... 147
5.1 Overview .......................................................................................................................147
5.2 Introduction ...................................................................................................................148
5.3 3D Printing of Bionic Leaf ...........................................................................................151
5.4 Thylakoid Isolation and Characterization .....................................................................152
5.4.1 Determination of the Chlorophyll Content in Isolated Thylakoids ........................154
xvi
5.5 Photosynthetic Electron Generation: Hill Reaction ......................................................155
5.6 Electronic Conduction Medium- Formulation and Characterization............................158
5.6.1 Characterization of Electronic Conduction Medium ..............................................159
5.7 Photosynthetic Material ................................................................................................162
5.8 Production for Photosynthetic Bioelectricity ................................................................163
5.9 3D Printable Bionic Leaf Architecture .........................................................................164
5.10 Conclusions .................................................................................................................165
5.11 References ...................................................................................................................166
Chapter 6 ....................................................................................................................................169
Conclusions and Future Outlook ..............................................................................................169
6.1 Summary of Main Conclusions ....................................................................................169
6.2 Future Outlook ..............................................................................................................172
xvii
List of Figures
Figure 1.1 Artistic rendition of bionic human.................................................................................2
Figure 1.2 Image of conventional cochlear implant system ...........................................................4
Figure 1.3 Ashby plots of biological and abiotic materials ............................................................7
Figure 1.4 Discrepancies between biological and engineered systems ..........................................9
Figure 1.5 Carbon nanomaterials ..................................................................................................13
Figure 1.6 Ambipolar field effect in graphene ..............................................................................14
Figure 1.7 Mechanical properties of graphene..............................................................................15
Figure 1.8 Semiconducting quantom dots.....................................................................................16
Figure 1.9 Metallic nanoparticles..................................................................................................17
Figure 1.10 Self assembly .............................................................................................................19
Figure 1.11 Bacteriophage and phage display biopanning ...........................................................20
Figure 1.12 Tissue Engineering Approaches. ...............................................................................22
Figure 1.13 Thesis Overview- Bionic Systems .............................................................................23
Figure 2.1 Biotransferrable graphene wireless nanosensor ..........................................................39
Figure 2.2 Graphene biotransfer and characterization ..................................................................41
Figure 2.3 Raman spectra of tooth enamel and Bombyx mori silk fibroin film ............................42
Figure 2.4 Biotransfer of the sensor onto skin ..............................................................................43
Figure 2.5 Return loss (S11) of the wireless sensing element. .....................................................44
Figure 2.6 Optical microscopy images of graphene on surfaces ……………… .........................45
Figure 2.7 Stability of sensor in running water. ............................................................................46
Figure 2.8 Structural integrity testing of sensor on bovine tooth enamel. ....................................47
Figure 2.9 Graphene functionalization with antimicrobial peptides. ............................................50
xviii
Figure 2.10 Single bacterium detection. .......................................................................................53
Figure 2.11 Wireless monitoring of S. aureus. .............................................................................55
Figure 2.12 Structural integrity testing of sensor integrated onto IV bag .....................................56
Figure 2.13 Tooth sensor monitoring of breath and saliva ...........................................................58
Figure 2.14 Impedance spectrum of the reader coil. .....................................................................65
Figure 2.15 Impedance spectrum of the sensing element. ............................................................68
Figure 2.16 Complex impedance spectrum of the sensing element. .............................................69
Figure 2.17 Electrical equivalent circuit of the wireless sensor-reader system.. ..........................70
Figure 3.1 AMP-based electrical detection of bacteria ................................................................83
Figure 3.2 Sensitivity of the AMP electronic biosensor ...............................................................85
Figure 3.3 Impedance spectra of various concentrations of E. coli O157:H7 ..............................86
Figure 3.4 The effect of the surface density of immobilized Magainin I .....................................88
Figure 3.5 Optical microscopy of the selectivity of AMPs...........................................................90
Figure 3.6 Impedance spectroscopy of the selectivity of AMPs...................................................92
Figure 3.7 Impedance spectra of the sensor after exposure to pathogenic bacteria ......................93
Figure 3.8 Impact of varying pH ...................................................................................................94
Figure 3.9 Real-time binding of bacteria to AMP biosensors .......................................................96
Figure 3.10 Schematic of the impedance spectroscopy measurement setup ..............................103
Figure 4.1 Three dimensional interweaving of biological tissue and electronics ......................115
Figure 4.2 Growth and viability of the bionic ear. ......................................................................118
Figure 4.3 Gross morphology of the 3D printed bionic ear ........................................................120
Figure 4.4 Biomechanical characterization of the 3D printed neocartilage tissue ......................122
Figure 4.5 Electrical characterization of the bionic ear ..............................................................125
xix
Figure 4.6 Resistivity measurements ..........................................................................................128
Figure 4.7 Images of the 3D printed ear auricle .........................................................................129
Figure 4.8 Image of neocartilage growth of the 3D printed ear ..................................................129
Figure 4.9 Images of the 3D printed left bionic ears at various stages of growth. .....................130
Figure 4.10 Electrical resistance of the coil antenna in culture ..................................................131
Figure 4.11 LIVE/DEAD® assay of chondrocytes.....................................................................132
Figure 4.12 DNA content standard curve obtained from calf thymus DNA ..............................133
Figure 4.13 DNA content in the 3D printed ear at various stages during culture .......................134
Figure 4.14 Hydroxyproline standard curve obtained from L-Hydroxyproline .........................135
Figure 4.15 GAG standard curve obtained from Chondroitin-6-Sulphate. .................................136
Figure 4.16 Tensile testing of 3D printed dog bone samples......................................................139
Figure 4.17 Hardness measurement of the 3D printed ear cartilage ...........................................140
Figure 5.1 Schematic illustration of the bionic leaf architecture. ...............................................147
Figure 5.2 3D Printed Bionic Leaf for Energy............................................................................151
Figure 5.3 Isolation of Thylakoids ..............................................................................................153
Figure 5.4 Microscopy characterizations of isolated thylakoids .................................................154
Figure 5.5 Determination of the chlorophyll content in the isolated thylakoids.........................155
Figure 5.6 Hill Reaction using DCPIP ........................................................................................156
Figure 5.7 Hill Reaction- change in absorbance of the sample ..................................................157
Figure 5.8 Schematic illustration of electrical interfacing of thylakoids ....................................158
Figure 5.9 Formulation of the electronic conduction medium....................................................159
Figure 5.10 XRD characterization of the electronic conduction medium.. ................................160
Figure 5.11 Raman spectroscopy of the electronic conduction medium ....................................161
xx
Figure 5.12 Formulation of the photosynthetic material.............................................................162
Figure 5.13 Characterization of the photosynthetic material. .....................................................163
Figure 5.14 Measurement of the photosynthetic current ............................................................164
Figure 5.15 CAD of the bionic leaf architecture .........................................................................165
1
Chapter 1
Bionic Systems: Introduction
1.1 Bionics
Bionics is defined as the study of mechanical systems that function like living organisms or parts
of living organisms [Oxford dictionaries]. It is believed that the term bionics is coined by Dr.
Jack E. Steele, MD (who was also a US Air Force colonel) around 1958. There are two possible
arguments about the etymology of the word bionic. Some suggest that a possible origin could be
from the technical term bion (pronounced bee-on) (from Ancient Greek: βίος), meaning 'unit of
life' and the suffix -ic, meaning 'like', with combined meaning of 'like life'
[http://en.wikipedia.org/wiki/Bionics]. Some other sources suggest that the word is formed as a
portmanteau of bi (as in life) + onics (as in electronics) [National Geographic, 2010]. Both of
the suggested origins and their implied meanings is fitting to the technical definition of the term
“Bionics” as well as represents the functionality of the class of systems that are formed in
general as a merger of biological systems and engineered functional electronic or mechanical
systems (Fig. 1.1).
2
Figure 1.1 Artistic rendition of bionic human [Image credit: EDN December 2011 original
source: ST Microelectronics].
1.2 History of Bionics: Implantable Devices and Prosthetics
The use of implanted technological aids and prostheses has long been in existence as a means to
compensate for injuries and deformations resulting from trauma or diseases1,2
. In general, these
primitive versions of bionics involved the use of metallic materials in the form of plates, screws
and other prosthesis for the creation of implants and repairing fractures3. For example, the use of
artificial tooth constructs made of wrought iron was prevalent among the Romans even as early
as the first century AD, as replacement teeth3. A major milestone in the development of
implantable devices as replacement parts was marked by the performance of a total hip
3
replacement in 19381. However, the lack of suitable materials and poor engineering designs of
these early implants made them less successful.
In more recent years, rapid progress in the field of microelectronics and semiconductor
device fabrication techniques has contributed immensely to the advancement of implantable
devices. For example, the first successful implantation of a cardiac pacemaker in 1958 made a
significant impact in the medical field. Examples of other major implantable medical devices
include retinal implants and cochlear implants for hearing disabled persons .The most recent
development in cochlear implantation is in the treatment of single-sided nerve deafness (Fig 1.2).
The implanted device has external and internal parts. The external device consists of a digital
sound processor microphone and a transmitting coil. The sound picked up by the microphone is
sent to the transmitting coil via the speech processor. The transmitter sends the signal through the
skin barrier to the internal implanted device utilizing electromagnetic induction. The internal
implanted device consists of an electronics package that leads to an electrode array shaped in the
form of human cochlea. The electronics converts the signal into electrical energy and is passed to
the electrode array. This stimulates the nerve fibers and the signal is carried to the brain via
auditory nerve and is recognized by the brain for sound.
4
Figure 1.2 Image of a cochlear implant system showing the external device and the internal
implant. [Image credit: NIH].
Review articles such as the one on cyborg devices2 and text books such as “Bionics” by
Nachtigall4 are good sources for an elaborate survey on implantable devices and prosthetic
bionic systems.
The original idea of bionic systems and cyborg organisms has advanced in the recent
years by taking advantage of the development of novel functional materials and advanced
fabrication techniques5-10
. Approaches for the direct multidimensional integration of functional,
electronic and mechanical components with viable biological systems could open up tremendous
opportunities across a broad array of disciplines in science and engineering11,12
. These range
from the realm of direct interfacing of functional electronic and mechanical elements with pre-
grown, mature biological tissue and systems, to the development of a seamlessly merged,
5
chimeric bionic system with advanced functionalities13-21
. For example, the ability to three-
dimensionally integrate functional electronics with biological cells and tissue could enable the
creation of bionic organs that can have tremendous impact in regenerative medicine, prosthetics,
and human-machine interfaces. In general, the creation of a functional integration between
engineered and biological systems could provide opportunities for enhancing human
performance2,22
. However, the design and implementation of such systems demands a
fundamental understanding of the inherent properties and disparities between the biological and
engineered systems and their composition.
The following sections will thus attempt to take a closer look at the biological and
engineered systems, consider their major differences in the properties and functionalities, and
discusses approaches that enable us to overcome these differences for the design and
development of multifunctional bionic hybrids.
1.3 Biological Materials and Systems
Biological materials are ubiquitous in nature and form the multipotent constituents of all
prokaryotic and eukaryotic living organisms23-26
. They serve a diversity of functions including
mechanical support as in the case of skeletal bones, conversion of chemical energy into
mechanical energy as in the case of muscle cells and tissue, and as a reservoir for essential
minerals as in the case of bones serving as source of calcium and phosphorous27
. Biological
materials such as enzymes perform catalytic reactions, whereas the main functions of cellular
membranes include acting as selective ion barriers in addition to providing structural support for
the organelles and subcellular components28
. Chloroplast organelles in green plants and
cyanobacteria perform the function of producing food via photosynthesis. Thylakoid grana in the
6
chloroplasts function as the centers of photosynthetic light reaction with the help of integral
membrane proteins, Photosystems I and II that perform light induced water splitting reactions
and many are the unique and amazing functionalities of naturally occurring biological
components29-33
. A thorough review of the composition and properties of biological materials
and systems is hence beyond the scope of this chapter.
Ashby and Wegst classify biological materials into the following four groups34
:
1. Polymers and polymer composites: Examples of which include, silk, tendon, ligaments
and exoskeletons of arthropods35-37
.
2. Elastomers: Elastomeric biogenic materials are characterized by the ability to undergo
large strains (stretchable). Examples include skin, muscle, blood vessels and individual
cells.
3. Ceramics and ceramic composites: These are mostly comprised of minerals. Examples
include, bone, teeth, shells and diatoms23,38,39
.
4. Cellular materials: These include lightweight materials such as feathers, interiors of beak,
wood and cancellous / spongy bone 25,40,41
.
Proteins and other biological materials are formed from the basic building blocks of 20
amino acids23
. The long molecular chains of structural proteins such as collagen, keratin, elastin,
chitin, resilin, actin, myosin and abductin can result in a range of elastic strengths through
hierarchical organization23,42
. In the case of hard biological materials such as bone and dentin a
mineral phase is embedded in a collagen based organic matrix. Another major class of biological
materials is cellular with a foamy structure resulting in high stiffness and low weight23
.
7
1.4 Disparity in Properties between Engineered Systems and Biological Systems
There exist major differences in properties between the engineered abiotic systems and
biological materials that prevent a seamless integration of the both. First of all, the design
principles used in biological system formation and engineered systems are very much different43-
46.
Figure 1.3 Ashby plots, Young’s modulus E (which corresponds to stiffness) versus strength for
a variety of biological and abiotic materials [image source: Knowles et al 43
Copyright 2011
Macmillan Publishers Ltd (Nature Publishing Group)
8
This difference often stem from the differences in the primary elemental constituents in
both the systems. For example, biological systems are dominated by light elements such as C, N,
O, H, Ca etc. and elements such as iron, chromium, nickel, etc. are very rarely found, certainly
not in metallic form which makes a wide difference in their mechanical properties27
(Fig.1.3).
Iron found in red blood cells exists in ionic forms bound to hemoglobin where its function is
chemical, to bind oxygen instead of mechanical. In contrast, structural materials found in
biological systems are either polymers or their composites with ceramic particles27
.
1.4.1 Dichotomy in Formation
Another strikingly major difference exists between abiotic engineered and biological systems in
the processes resulting in their formation47-52
. Biological systems and materials are grown, (not
made) in to a whole organism (plant or animal) via self-assembly, guided by the principles of
developmental biology. As a consequence, biological systems are, in general, able to reconfigure
and adapt to environmental changes and self-heal when damaged. In addition, the biologically
controlled self-assembly driven growth takes place at near room temperature at atmospheric
pressure under common physiological conditions53,54
. In contrast, abiotic electronic or
mechanical systems are fabricated from the selected materials based on secure engineering
design considering extreme conditions. This design driven fabrication process often involves
high temperatures, pressure and what is considered to be “biologically harsh” chemical
conditions. The following figure (Fig.1.4) illustrates some of the key differences in properties
and functionalities between the two classes of materials and systems originating from the
fundamental disparity in the growth and fabrication processes.
9
Figure 1.4 Discrepancies in the elemental composition and mode formation of biological and
engineered systems [source: Fratzl et al 27
].
1.4.2 Limitations of Current Fabrication Methods
The inherent limitations of the current machining and fabrication methods allows only for a
static process. In general, an engineered electronic or mechanical system is designed and the
constituent materials are selected taking into account the functionalities, requirements and other
lifetime issues such as fatigue during service. In contrast, biological materials and systems are
grown and thus enables for a dynamic process allowing adaptation to environmental factors55-57
.
Here the problems of fatigue are taken care of using a constant renewal of materials by growth.
Further, the growth process allows for extremely complicated three dimensional integration of
various functional materials in a single system. Organs of animals and parts of plants such as
10
leaves represent very good example of such hierarchical integration of materials and structures
achieved via the growth process. As a consequence, biological systems can also be functionally
graded with hierarchical structures, a property that is hard to achieve via conventional
fabrication methods58
. Examples of such hierarchical structures in biogenic tissue consisting of
completely different composition include: wood-a total polymeric structure, glass sponges-
composed entirely of silica and bone ( an organic-inorganic composite) consisting of
approximately half polymer and half mineral27
.
1.5 Overcoming the Differences: Nanoscale Science and Engineering
Nanoscale science and engineering offers a general strategy to overcome the
discrepancies between the biotic and abiotic worlds. Despite the dichotomies existing between
the two classes of materials and systems, going down on the size scale to the dimensions of the
fundamental building blocks in the micro and nano regimes in each group allows for a
synergistic integration. This symbiosis arises as a consequence of the natural compatibility that
lies between biomolecules and the nanoscale inorganic electronic and structural materials. Such
an interconnect could be aided by two factors: size and electronic charge. For example, the size
scale of DNA duplex, protein molecule, viral particle are in the order of 1nm, 10nm and 100nm
respectively. In comparison, the diameter of a single walled carbon nanotube is about 1nm and
the cross section of fabricated semiconductor nanowire is in the order of 10nm. This size
similarity makes ‘Nano’ the natural length-scale for functional abiotic interfaces with biological
systems59
. The second feature that aids the linkage between the two classes of materials is the
electronic charge. The charge distribution and localized electric dipoles in biological molecules
are crucial in attaining wide variety of their functionalities.
11
Nanotechnology enabled bio-orthogonal tools and processes utilize this dimensional
similarity and charge based affinity between biological materials and abiotic functional
nanomaterials to create a symbiotic integration as described in detail in the following sections.
Here the term “bio-orthogonal” is used to identify/qualify nanoscale materials and
bionanotechnology processes that enable to control, probe and modify biological systems
without interfering their native processes but can in fact complement and enhance their natural
functionalities.
1.5.1 Nanoscale Mechanics: Influence of Size on Mechanical Behavior
Biological systems are organized hierarchically, with unique characteristics and functionalities
spanning multiple length scales which demands the selection of the right organizational length
scale for biointerface design. In the case of sub-cellular organization, this length scale is
determined by the size of individual organelles which are on the order of tens to hundreds of
nanometers. Enabling a close contact is the key element in the success of integration between the
biological and man-made systems2. The integration should be achieved to such a degree that the
contact points of the engineered system/machine comes to the size range of the biological
functional unit2. In the case of biogenic organs, tissues, and cells, this size range extends from
centimeters to nanometers ( for example, in the case of nerves in muscle tissue, they are the
order of centimeters while in the case of ion channels of individual nerve cells, they are of the
order of nanometers)2. Further, the quality of the interfacing between organism and machine is
further increased with the mechanical compatibility. As an illustration, arrays of electrodes
mounted on flexible and stretchable materials were in order to address the mechanical
requirements of soft, deformable tissue. For example, Rogers et al have developed stretchable
form of electronics from various materials including single-walled carbon nanotubes and single-
12
crystal micro- and nanoscale wires and ribbons of gallium nitride, silicon, and gallium arsenide
on flexible substrates22,60
. Further, the influence of Van der Waals forces increases as the size
scale of the structures reduces to nanoscale. This often provides a high degree of adhesion
energy for the nanoscale abiotic functional materials for biointerfacing applications. Thus, in
terms of achieving a high fidelity interfacing, functional electronic and structural nanomaterials
are a size-compatible fit, allowing for bottom up integration and building of multifunctional
bionic systems.
1.6 Nanoscale Functional Electronic and Structural Materials
Functional nanomaterials are capable of exhibiting a wide range of configurations, allowing for
facile integration with the biological systems61
. Over the past decades, several such
nanomaterials exhibiting size dependent properties that are distinct from the bulk were realized
and studied. Among such nanoscale building blocks, carbon nanotubes (CNTs), graphene,
metallic nanoparticles, quantum dots (QDs) and semiconducting nanowires (NWs) gained much
attention and a brief summary of their functional properties are described below.
Materials in the nanometer dimension, in general, possess interesting functional
properties, originating mainly from the quantum confinement effect62
. The confinement of the
charge carriers in these nanoscale materials influences their density of states, leading to size and
shape dependent properties. Such ability to tune the functional properties of the materials without
changing the chemical constituency has opened up a variety of applications in biomedicine and
engineering. In addition, fine tuning of the properties of these nanomaterials can be further
attained via integration into hybrid systems consisting of inorganic-inorganic or inorganic-
13
organic interfaces. These properties make nanoscale functional materials ideal building blocks
for the bottom-up creation of multi-functional bionic systems and devices63,64
.
1.6.1 Carbon Nanomaterials and Graphene
Carbon is the starting material for life and as a consequence of its flexibility in chemical bonding
it exists in unlimited forms of structures, exhibiting a variety of physical properties65
. Most of
the physical properties of the carbon structures are dependent on their physical size and shapes.
Graphene is a 2D allotrope of carbon arranged in a honeycomb lattice (Fig. 1.5). Fullerenes
represent zero dimensional objects with carbon atoms arranged in a spherical structure and from
a physical point of view can be thought of as wrapped up graphene. Carbon nanotubes (CNTs)
are one dimensional objects and can be thought of as rolled up graphene with reconnected ends.
Graphite, the three dimensional allotrope of carbon is made up of stacks of graphene layers.
14
Figure 1.5 Graphene is a 2D building material for carbon materials of all other dimensionalities.
It can be wrapped up into 0D buckyballs, rolled into 1D nanotubes or stacked into 3D graphite
[Image source: Geim et al 66
] Copyright 2007 Macmillan Publishers Ltd (Nature Publishing
Group)
The most notable feature among the electronic properties of graphene is its ambipolar
field effect characteristics- its ability to continuously tune the charge carriers from electrons to
holes (Fig. 1.6) Further, at low temperatures and high magnetic fields, graphene exhibits
quantum Hall effects as a consequence of its exceptional mobility. The quantum Hall effect in
graphene is observed to show plateaus at half integer multiples of instead of the
conventional integer multiples of , believed to be a consequence of its unique band
structures. The strong gate dependence of graphene conductance makes it an ideal nanomaterial
transducer for sensing applications.
15
Figure 1.6 Ambipolar field effect in graphene [Image source: Geim et al66
] Copyright 2007
Macmillan Publishers Ltd (Nature Publishing Group)
In addition to the remarkable electronic properties67
, the mechanical properties of
graphene also make it a stand out material (Fig. 1.7). Graphene has an ultimate tensile strength of
~130 GPa68
. Atomic microscopic (AFM) tests conducted on graphene sheets suspended over
silicon dioxide cavities exhibited a Young’s modulus (different to that of graphite) of 1 TPa68
.
Van der Waals forces play a major role in the mechanical behavior of graphene by keeping its
individual layers together as well as holding it “clamped” to a substrate69
. Pressurized blister
tests performed on graphene layers on silicon dioxide substrates directly measured the adhesion
energy to be 0.45 ± 0.02 J/m2 for monolayer graphene and 0.31 ± 0.03 J/m
2 for samples
containing 2-5 graphene sheets70-72
. These values are comparable to solid/liquid adhesion
energies and are comparatively higher than what is typically seen in micromechanical
structures70
.
Figure 1.7 Blister test for adhesion on graphene [Image source: Huang et al 64
]. Copyright 2011
Macmillan Publishers Ltd (Nature Publishing Group)
This surprisingly high value of adhesion energy is believed to be the result of high level of
flexibility exhibited by graphene layers that allows for a conformal lamination against the
16
surface of a substrate. These unique electronic and mechanical properties make graphene an ideal
nanomaterial building block for bio-interfacing applications.
1.6.2 Semiconducting Quantum Dots
These are nanocrystals consisting of semiconducting materials which exhibit quantum
mechanical properties as a consequence of their small size scales73
. When the semiconducting
material is confined in physical dimensions to size scales that are comparable or lower than the
exciton Bohr diameter, its functional properties will become sensitive to the size and shape as a
result of quantum confinement effect62
. The excitons in QDs are confined in all three spatial
directions and hence they exhibit electronic properties that are between that of bulk material and
single molecules74,75
.
Figure 1.8 Quantum dots with vivid colors stretching from violet to deep red. [Image
courtesy: Antipoff, Wikipedia, previously published: www.plasmachem.com].
Electronic characteristics of quantum dots are thus highly influenced by their size and shape.
Since the band gap of quantum dots is related inversely to their size, the frequency of emitted
light increase as the size decreases. This allows for highly tunable optical properties, thus making
17
the semiconducting quantum dots very interesting for applications such as light emitting diodes
(LEDs), solar cells and in biomedical imaging76
.
1.6.3 Metallic Nanoparticles, Nanowires and Nanorods
Nanoscale objects made of noble metal elements such as gold (Au) and silver (Ag) have unique
optical, electrical and thermal properties that make them interesting for a wide range of
applications (Fig. 1.9). Examples include, applications in electronics as conductive inks taking
advantage of their high electrical conductivity and molecular diagnostics and photonic devices
utilizing their novel optical properties77
. Near-IR absorbing gold nanoparticles produce heat
when excited by light at wavelength corresponding to their surface plasmon resonce (SPR),
making them interesting for applications such as plasmonic photothermal antenna. Additional
applications include diagnostics and in catalysis of chemical reactions.
Figure 1.9 (A) Localized surface plasmon resonance in nanoparticles.( B) Various forms of
nanoparticles (A) gold nanospheres, (B) nanorods, (C) nanoshells, (D) nanocages. [Image
source: Claire et al 77
]. Copyright 2010 Royal Society of Chemistry
18
The conduction electrons at the surface of the metallic nanoparticles undergo collective
oscillation at specific wavelengths corresponding to their SPR resonance. As a consequence they
exhibit strong scattering and absorption properties. These SPR peak wavelengths can be tuned in
a broad range from visible to infra-red regions by simply modifying the size and shape of the
metallic nanoparticles.
1.7 Bio-orthogonal Approaches for Bionic Integration
A seamless engineering of bio-abio interface can be achieved from the nanoscale building blocks
utilizing a set of tools and approaches that enable probing the biological world without
perturbing its natural functionality. Such bio-orthogonal tools are generally grouped under the
broader umbrella of Bionanotechnology78-82
.
1.7.1 Biomimetics: Engineering biocompatibility via biomimicry
Engineering biocompatibility between viable biological systems and functional abiotic materials
is a significant step in achieving an efficient bio-abio interface83-87
. It is often the case, that the
best material suitable for achieving the most efficient engineered device functionality does not
always fulfill the material characteristics necessary for biocompatibility88-90
. Biomimicry offers a
means of modification of functional materials, at macro- and mesoscopic scales, so as to render
them more biocompatible for bionic integration when compared to their unmodified states91-93
.
Chemical functionalization, modification and derivatization of surfaces are often used as a way
to impart biomimetic features to a material. Further, modification of the mechanical properties of
engineering materials to mimic the surrounding tissues of biological systems can also improve
biocompatibility94
.Mechanical property of tissues and organs in body varies in a wide range and
hence matching the mechanical properties of the engineered materials to that of host tissue is a
19
significant part in the bionic device design. Typically the bio-abio interface is constructed
through a cascade of protein and cellular interactions that are determined by the composition and
physical structure of the materials that make up the bionic systems.
1.7.2 Self- Assembly
Self-assembly is the primary approach that natural biological systems make use of for their
formation95
. A beautiful example of self-assembly in a biological system is a bacteriophage (Fig.
1.10). Once broken up in a blender, phages have been shown to have the ability to reassemble in
a test tube in a quasi-mechanical way without the use of any additional templates23
. Further, self-
assembly serves as a powerful tool in achieving nano-scale bionic interfaces. For achieving a
bionic integration, self-assembly serves as a bridge between the top-down approaches and
bottom-up methods96,97
. It makes possible the patterning or hierarchical integration of
nanostructures made by bottom up synthesis in a programmable manner96-99
. In general, self-
assembly serves as the best method in bionic integration scenarios where, the components are too
small for top down, there are too many components for conventional placement, a
multidimensional integration is desired or when the fragility of the biological molecular
components is an issue100,101
.
20
Figure 1.10 Self-assembly (A) Schematic illustration of broken down phage particles
spontaneously self-assemble to the full organism [image adapted from Meyers et al 23
] Copyright
2008 Elsevier.
1.7.3 Phage display
An interesting application of bacteriophages in molecular biomimetics is using them to find
proteins that show unique surface interactions with functional inorganic substrates23
. Naturally
occurring biomolecules such as proteins and peptides are formed via evolutionary processes 102
.
Combinatorial biology techniques such as phage display (PD) enable to create artificial
biomolecules that mimics the naturally occurring proteins for technological applications102,103
.
Conventionally, phage display has been used in biomolecular engineering for the selection of
ligands for proteins and peptides (Fig. 1.11)104-106
. Over the past decades this combinatorial
approach had been adapted and modified to be a powerful bio-orthogonal tool to select material-
specific peptides107-110
.
Figure 1.11 Phage display biopanning to select graphene binding peptides [image source: Cui et
al 111
] Copyright 2010 American Chemical Society.
21
Such phage display based forced evolutionary strategies called in-vitro selection, has
enabled finding of peptide linkers for variety of functional nanomaterials including metallic,
semiconducting and carbon nanomaterials112
.
1.7.4 Tissue Engineering
Tissue engineering utilizes interdisciplinary strategies from various biological sciences and
engineering disciplines to develop and grow bioartificial tissues or organs for applications in
regenerative medicine113,114
. Typically, scaffolds are used to provide cells with mechanical
support and a growth environment with sufficient supply of gaseous and liquid media (Fig. 1.12).
This enables to bring cells in close proximity in a 3D environment, so that they can assemble to
form tissues115,116
. When supplied with sufficient nutrition under the appropriate growth
conditions, the scaffold is degraded and the cells deposit their own extracellular matrix (ECM)
molecules and self-assemble to form 3D tissue structures115,117
. For bionic systems engineering
applications, tissue engineering thus serves as a powerful technique that draws on the principles
of developmental biology to mimic the nature’s way of growth process in creating living bionic
systems64
. Further, incorporation of novel functional materials and the utilization of improved
fabrication techniques can significantly improve the functionality of the grown systems.
22
Figure 1.12 Tissue Engineering Approach. Schematic illustration of tissue engineering
approaches [image source: Khademhosseini et al 115
].
1.8 Additive Manufacturing for Bottom-up Three Dimensional Integration
Additive manufacturing such as 3D printing enables the creation of three dimensional (3D)
structures, in a layer by layer fashion, following a desired pattern. As a consequence, the amount
of material wasted during an additive manufacturing process is minimal, in contrast to the
conventional fabrication techniques that typically utilizes the removal of material from a bulk
substrate. 3D printing based additive manufacturing techniques thus serve as a unique tool to
enable multidimensional integration of a variety of abiotic and biotic functional materials such as
electronic, mechanical, biomaterials and biological cells. When paired with other bio-orthogonal
processes, this approach offers a strategy for simultaneous three dimensional integration between
biological components and abiotic functional nanomaterials in a precise 3D- geometry,
prescribed by a computer aided design (CAD) file to enable the creation of novel bionic hybrids
possessing unique functionalities.
23
1.9 Thesis Overview
This thesis presents a study on the design, development and characterization of a number of
prototype bionic systems with applications in biomedical and energy fields.
Figure 1.13 Thesis Overview- Bionic Systems. Schematic illustration of the three bionic systems
with applications in biomedical and energy presented in succeeding chapters of this thesis. (left)
Bionic Nanosensor, (middle) bionic organs and (right) bionic leaf.
The next chapters of this thesis are organized as follows: Chapter 2 presents the design,
development and testing of biointegrated nanosensors for ubiquitous biomedical sensing
applications. Chapter 3 presents the details of the characterization study on the antimicrobial
peptide based biological molecules, directly integrated on to electronic sensors to act as
bioprobes for bacterial sensing. Chapter 4 discusses the creation of bionic organs with three
dimensionally integrated electronic, structural and biological components using nanomaterials
engineering and additive manufacturing techniques. This concept is illustrated by discussing the
creation of a bionic ear with embedded electronics in a tissue engineered cartilaginous ear
auricle. Chapter 5 presents the design and development of bio-inspired systems for energy, such
as the creation of a bionic leaf, enabled by integrating plant derived photosynthetic functional
24
units with electronic materials and components into a leaf-shaped hierarchical structure, for
harvesting photosynthetic bioelectricity. Finally, the thesis concludes with a summary of the
research and discussion on future directions.
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35
Chapter 2
Bionic Nanosensors§
2.1 Overview
Direct interfacing of nanosensors onto biomaterials could revolutionize health quality
monitoring and adaptive threat detection. Graphene is capable of highly sensitive analyte
detection. Here we show that the nanoscale nature of graphene allows it to be printed onto water-
soluble silk. This in turn permits intimate biotransfer of graphene nanosensors onto biomaterials,
including tooth enamel. The result is a fully interfaced sensing platform which can be tuned to
detect target analytes. For example, via self-assembly of peptides onto graphene, we show
bioselective detection of bacteria at single cell levels. Incorporation of a resonant coil eliminates
the need for onboard power and external connections.
Combining these elements yields two-tiered interfacing of peptide-graphene nanosensors
with biomaterials. In particular, we demonstrate integration onto a tooth for remote monitoring
of respiration and bacteria detection in saliva. Overall, this strategy of hierarchically interfacing
biomolecules with nanosensors and biomaterials represents a versatile approach for detecting
biochemical targets.
2.2 Biointegration of Sensors
§ The work reported in this chapter is based on the following original publication: Mannoor, M. S.; Tao, H.; Clayton,
J. D.; Sengupta, A.; Kaplan, D. L.; Naik, R. R.; Verma, N.; Omenetto, F. G.; McAlpine, M. C., Graphene-based
wireless bacteria detection on tooth enamel. Nature Communications 2012, 3, 763.
36
Interfacing electronic devices and sensors with biomaterials has been of interest for decades, for
on-body physiological and analytical measurements1-3
. Traditionally, device designs for such
applications involved either implantation of device electrodes into tissue4, or mechanical
mounting of components on the body using braces, clamps or adhesive tapes. Such systems
encased rigid and bulky onboard power sources, associated circuitry, and direct physical
connections between the sensing probes and data processing electronics5,6
. Further, the large
form factors and rigid substrates prohibited intimate integration on the soft and curvilinear
surfaces of biological tissues, causing discomfort during continuous use. Device designs and
platforms that minimize the mechanical discrepancy between such abiotic/biotic interfaces are
thus highly desired for conformal biointegrated electronics and sensors.
Electronic sensors based on nanoscale materials such as nanowires7, carbon nanotubes
(CNTs)8, and graphene
9 have been shown to boast parts-per-billion (ppb) sensitivities, a
consequence of the high surface areas of these materials. CNT-based composite materials with
passive circuits have enabled wireless chemical and gas sensors10
. Single-atom-thick, sp2
graphene is a particularly interesting material due to its remarkable electrical11
, mechanical12
,
and sensing13,14
properties. The growth of graphene films on supporting metallic films (Ni or Cu)
using chemical vapor deposition (CVD) methods15
, combined with post-etching of the
underlying metal, offers the ability to efficiently transfer graphene films to other substrates over
large areas16
for biocompatible sensing and flexible electronics applications17,18
. This is enabled
by graphene’s intrinsic strength of 42 N/m and Young’s modulus of ~1 TPa19
, as well as the high
interfacial adhesion exhibited by graphene to substrates (adhesive energy of 0.45 J/m2 on
SiO2)20
. These properties render graphene an ideal active material for direct interfacing onto
rugged surfaces.
37
Silk, a textile industry staple for thousands of years, has recently sparked increased
interest within the materials science community due to its impressive mechanical properties
including high elastic modulus, tensile strength, ductility, and toughness21,22
. As a result, silk
films have been shown to be an efficient “middleman” medium for transferring materials such as
passive metallic electrodes onto tissues via intimate contact and dissolution – a consequence of
the elasticity and biodegradability imparted by the unique molecular structure of silk. Silk films
have been patterned with metal electrodes and intimately “bioresorbed” onto brain and skin
tissues for electro-mapping experiments21,23
. Recent work has demonstrated the ability to
fabricate active electronic components such as transistors24
and metamaterials25
on films of
regenerated silk.
In addition to sensor sensitivity, selectivity toward defined chemical and biological
targets is a challenging goal in which bioinspired approaches are particularly useful. Aptamer
functionalized nanotube electrodes have been shown to detect single bacterial cells in real time26
.
Further, we have recently shown that phage display can be utilized to determine peptide
sequences which selectively bind to CNTs and graphene8,27-29
. This has enabled the generation of
bifunctional peptides containing a carbon nanomaterial recognition moiety combined with an
analyte binder to noncovalently self-assemble and impart selectivity on graphene sensor arrays.
Our recent study has demonstrated the ability of naturally occurring antimicrobial peptides
(AMPs) to serve as robust biorecogniton moieties in electronic biosensing platforms30
(please see
chapter 3 for details). Unlike antibodies, AMPs are significantly more stable and exhibit
broadband detection for a range of pathogenic bacteria31,32
.
Pathogenic contamination and resistant “superbug” infections remain critical concerns in
both developed and developing nations, due to extremely low minimum infective doses (MID)
38
for many bacteria and the lack of inexpensive and portable methods to detect at these limits33
.
Currently available methods for the detection of microbiological threats utilize specific
enrichment media to separate, identify and count bacterial cells26
. Alternatively, polymerase
chain reaction (PCR)34
and DNA-based nanobarcode35
detection strategies have proven to be fast
and highly sensitive, but such methods require pretreatment and cell lysis to extract DNA. An
alternative strategy is the development of methods that allow for direct and sensitive detection of
whole microbial cells or endotoxins. Particularly interesting would be sensors that could be
directly interfaced with contamination sources, including the body, food, and hospital equipment.
Here we describe a novel approach to directly interfacing passive, wireless graphene
nanosensors onto biomaterials via silk bioresorption. First, graphene nanosensors are
comprehensively printed onto water-soluble silk thin film substrates. The graphene is then
contacted by interdigitated electrodes, which are simultaneously patterned with an inductive coil
antenna. Finally, the graphene/electrode/silk hybrid structure is transferred to biomaterials such
as tooth enamel or tissue, followed by functionalization with bifunctional graphene-AMP
biorecognition moeities. The resulting device architecture is capable of extremely sensitive
chemical and biological sensing, with detection limits down to a single bacterium, while also
wirelessly achieving remote powering and readout. The generation of “biotransferrable” sensors
combined with high sensitivity and selectivity may provide a first line of defense against
pathogenic threats at the point of contamination.
2.3 Results & Discussion
2.3.1 Graphene/silk sensor
39
The fundamental operation and key functionalities of the sensor design are schematically
illustrated in Fig 2.1. First, a graphene-based sensing element with wireless readout coil is
generated on silk fibroin (Fig. 2.1a). Next, the ultra-thin nanosensors are intimately
biotransferred from the silk platform onto biomaterials, such as tooth enamel, via dissolution of
the supporting silk film (Fig. 2.1b). The extremely large surface area of the graphene and
electrodes ensures high adhesive conformability to the rugged surfaces of biomaterials.
Specificity in biological recognition is achieved by self-assembling designer bifunctional AMP-
graphene peptides onto the graphene monolayer (Fig. 2.1c), such that non-covalent
functionalization of graphene can be achieved without degrading its electronic sensing
properties. Further, Figure 2.1c illustrates the two other major functionalities of the hybrid
biosensor unit: battery free operation, and remote wireless sensing capability. Upon recognition
and binding of specific bacterial targets by the immobilized peptides (Fig. 2.1d), the electrical
conductivity of the graphene film is modulated and wirelessly monitored using an inductively
coupled radio frequency (RF) reader device. The key functionalities of the graphene/silk hybrid
sensing elements are thus derived from a synergistic integration of the individual materials
properties and components.
Figure 2.1 Biotransferrable graphene wireless nanosensor. (a) Graphene is printed onto
bioresorbable silk and contacts are formed containing a wireless coil. (b) Biotransfer of the
40
nanosensing architecture onto the surface of a tooth. (c) Magnified schematic of the sensing
element, illustrating wireless readout. (d) Binding of pathogenic bacteria by peptides self-
assembled on the graphene nanotransducer.
2.3.2 Materials integration and characterization.
Large area graphene monolayers are integrated with water soluble silk fibroin films (ca. 50
microns thick) using a simple transfer printing process (Fig. 2.2a, see Methods). Electrode
patterns are then incorporated onto the silk-graphene hybrid films via shadow mask assisted
electron beam evaporation of gold to generate the biosensor (Fig. 2.2b). Specifically, the
architecture consists of a parallel LRC resonant circuit with a gold inductive coil for wireless
transmission, and interdigitated capacitive electrodes contacting graphene resistive sensors. The
resulting device is a passive wireless telemetry system, obviating onboard power sources and
external connections. The thin film sensing elements thus fabricated on silk are then
biotransferred and intimately integrated onto a variety of substrates. Complete dissolution of the
silk matrix template in water led to strong attachment of the graphene-Au electrode structure
within a time period of 15-20 minutes. Significantly, Figure 2.2c shows a photograph of the
graphene nanomaterial with patterned gold electrodes integrated onto the surface of a human
molar, and Figure 2.2d shows a photograph of the graphene sensor biotransferred directly on
muscle tissue. To ensure complete dissolution of the silk substrate, we performed sensor
biotransfer experiments using fluorescent silk films, before and after the dissolution of the silk
(Fig. 2.2e, left). Complete quenching of fluorescence was verified after immersion in water for
20 min (Fig. 2.2e, right). Electronic and structural properties of the graphene were interrogated
using Raman spectroscopy36
: Figure 2.2f shows the Raman spectrum of graphene following
biotransfer onto a tooth surface
41
Figure 2.2 Graphene biotransfer and characterization. (a) Graphene printed onto bioresorbable
silk film. (b) Passive wireless telemetry system consisting of a planar meander line inductor and
42
interdigitated capacitive electrodes integrated onto the graphene/silk film. (c,d) Graphene
nanosensor biotransferred onto the surface of a human molar (c), and onto muscle tissue (d).
Scale bars are 5 mm. (e) Fluorescent image of sensor fabricated on a fluorescent silk film and
laminated onto the surface of a tooth, before (left) and after (right) dissolution of silk. Absence of
fluorescence signal confirmed complete removal of the silk matrix. Scale bar is 250 µm. (f)
Raman spectrum following interfacing of graphene onto the tooth surface.
The spectrum is in good agreement with other graphene monolayer spectra36
, and the
phosphate ν1 peak from the tooth enamel substrate is evident37
. Raman spectra of the bare tooth
enamel and silk fibroin film are provided in Fig. 2.3.
Figure 2.3 Raman spectra of tooth enamel and Bombyx mori silk fibroin film. Raman spectra of
(a) bare tooth enamel surface (b) silk fibroin substrate. The amide band at 1660 cm-1
indicates
the presence of domains of silk I structure in the silk film38
.
43
Sensor integration on human skin is shown in Fig 2.4
Figure 2.4 Biotransfer of the sensor onto skin. (a) Optical image of the graphene based wireless
sensing element on a water soluble silk fibroin substrate. (b) Conformal transfer of the sensing
element onto human skin via the dissolution of the supporting silk substrate. (c) Magnified
optical image of the sensor after transfer. Scale bars are 7 mm.
A full-wave electromagnetic simulation tool, Ansoft HFSS, was utilized to simulate and
design the planar coil antenna and interdigitated capacitive electrode geometries (Figure 2.5).
44
Figure 2.5 Return loss (S11) of the wireless sensing element. The S11 parameter of various
designs of the wireless sensing element was simulated using Ansoft HFSS software. Inset shows
the schematic of the LC design (left) and image of the design implemented on a Si chip (right).
Optical characterization of the transferred graphene revealed good structural integrity
(Fig. 2.6)
45
Figure 2.6 Optical microscopy images of graphene on surfaces. (a) Optical microscope image of
graphene film on Ni surface. (b) Optical microscope image of graphene transferred onto a
surface via the dissolution of the silk film.
For sensors interfaced with skin, no degradation or delamination was observed following
mild rinsing in running water as shown in Fig. 2.7.
46
Figure 2.7 Stability of sensor in running water. Optical images of (a) biotransferred sensor onto
a human arm, (b) mild rinsing in running water, and (c) the sensor following exposure to running
water. Scale bars are 1 cm.
47
The mechanical stability of the sensor on tooth enamel was analyzed via agitation in
commercial mouthwash for a period of 3 min followed by comparative Raman spectra analysis
(Fig. 2.8)
Figure 2.8 Structural integrity testing of sensor biotransferred onto bovine tooth enamel. Optical
images of (a) sensor interfaced on tooth before testing, (b) immersion of the tooth in mouthwash,
(c) vortexing of the tooth sensor in mouthwash, (d) structurally intact sensing element after
vortexing, and (e) the tooth after removal from the solution. All scale bars are 1 cm. (f) Raman
48
spectrum of the graphene surface before vortexing. (g) Raman spectrum of the graphene sensor
after vortexing in mouthwash, showing higher edge-induced D band intensity39
.
2.3.3 Functionalization of graphene with AMPs
The ability to specifically detect various species of pathogenic bacteria is useful for biomedical
applications and food, water, and air quality monitoring. Our previous study30
demonstrated that
AMPs may serve as robust biorecognition molecules with broad-spectrum activity towards
various pathogenic bacteria. Further, we have recently shown that phage display can be utilized
to determine peptide sequences which selectively bind to carbon nanomaterials8,27,40
. Here,
graphene nanosensors were functionalized with a chemically synthesized bifunctional peptide,
consisting of 1) a dodecapeptide graphene binding peptide (GBP), 2) a triglycine linker, and 3)
the AMP odorranin-HP (OHP), which shows activity toward both the Gram-negative bacteria E.
coli and H. pylori and the Gram-positive bacteria S. aureus41
. Figure 2.9a shows a molecular
drawing of the resulting 38 amino acid sequence, HSSYWYAFNNKT-GGG-
GLLRASSVWGRKYYVDLAGCAKA (GBP-OHP). Raman spectroscopic analysis of the
peptide functionalized graphene surface indicated slight doping of graphene (Fig. 2.9b),
consistent with our previous electronic measurements40
.
The activity of the immobilized GBP-OHP toward S. aureus and H. pylori cells were
compared via fluorescent assays with activity toward erythrocytes (Figs. 2.9c, 2.9d and 2.9e
respectively). The concentrations of bacterial cells used for the assays was 106 CFU/mL and the
concentration for erythrocytes was 40% hematocrit. The assays clearly show higher binding to
bacterial cells, evident by the higher fluorescent density. The specificity of the interaction of S.
aureus cells with GBP-OHP peptides was further analyzed via flow-through electrical
49
measurements of the graphene sensors (Fig. 2.9f). Following elution with DI water, the response
of GBP-OHP toward S. aureus is four-fold larger than the response toward both a GBP
functionalized sensor and a GBP-OHP sensor exposed to erythrocytes.
50
51
Figure 2.9 Graphene functionalization with Antimicrobial peptides. (a) Molecular model of a
bifunctional peptide consisting of a graphene binding peptide (GBP) coupled to an antimicrobial
peptide odorranin-HP (OHP) via a triglycine linker (-GGG-). (b) Raman spectra before (blue
line) and after (red line) immobilization of bifunctional peptides on the graphene surface. The
inset shows a shift in the 2D band of graphene due to molecular doping. (c-e) Fluorescent images
of the binding of S. aureus (c), H. pylori (d), and erythrocytes (e) to GBP-OHP functionalized
graphene. Scale bars are 10 μm. (f) Selectivity of GBP-OHP functionalized graphene sensor. ( )
Indicates resistance of graphene sensor functionalized with GBP-OHP upon exposure to DI
water. ( ) Indicates resistance of graphene sensor functionalized with only GBP upon exposure
to S. aureus. ( ) Indicates resistance of graphene sensor functionalized with GBP-OHP upon
exposure to erythrocytes. ( ) Indicates resistance of graphene sensor functionalized with GBP-
OHP upon exposure to S. aureus. Dotted line indicates elution with DI water. Inset shows image
of the flow-through measurement system. Scale bar is 1 cm. Concentrations of the bacterial cells
used for the assays is 106 CFU/mL, and the concentration of erythrocytes is 40% hematocrit.
2.3.4 Single Bacterium Detection
Detection of bacteria at the single-cell level is a critical goal for biosensors due to the
extremely low MID of many bacteria18,33,42
. To investigate the responsiveness of the graphene
nanosensors towards single bacterial cells, time-dependent resistance data and optical
measurements were carried out in parallel. Importantly, as shown in Figure 2.10a, simultaneous
collection of electrical and fluorescence data from bare graphene sensors in the presence of
fluorescently labeled E. coli cells clearly indicate a discrete change in electrical resistance
corresponding to the binding and unbinding of a single bacterial cell from the graphene surface.
The approximate 0.6% decrease in resistance due to binding of bacteria is readily explained by
52
the fact that Gram-negative bacteria such as E. coli possess an outer membrane with negatively
charged lipopolysaccharide (LPS), indicating p-type behavior of the graphene transducer
consistent with other studies11
.
Next, we determined the effect of the immobilized AMPs on bacterium binding. The
inset of Figure 2.10b shows a fluorescent image of the graphene nanosensor functionalized with
FITC-labeled GBP-OHP. The result suggests uniform coverage of the graphene surface with
peptides and selective recognition of the peptide toward graphene relative to the gold electrodes.
Simultaneous resistance and optical data were recorded on graphene sensors functionalized with
GBP-OHP (Fig. 2.10b). Significantly, compared to the bare graphene nanosensor (Fig. 2.10a),
peptide-coated electrodes display bacterium binding without concomitant unbinding, suggesting
a strong interaction between the bacterium and immobilized peptides.
53
Figure 2.10 Single bacterium detection. (a) Electrical resistance (upper) and fluorescence
(lower) data recorded simultaneously vs. time showing binding/unbinding of a single E. coli
bacterium on a bare graphene nanosensor. Images are (12 μm)2. (b) Resistance (upper) and
optical (lower) data recorded simultaneously vs. time showing binding of a single E. coli
bacterium on a peptide-functionalized graphene nanosensor. Images are (20 μm)2. Inset shows
54
fluorescent image of peptide functionalized graphene surface (green), with the black regions
representing electrodes. Scale bar is 250 µm.
2.3.5 Wireless Remote Query Monitoring of S. aureus.
A major functionality of the sensor construction is the wireless remote query capability. Certain
strains of S. aureus are notoriously antibiotic-resistant and responsible for over 500,000 post-
surgical wound infections in the US each year43,44
. S. aureus has been reported to survive up to 9
weeks on standard plastic and similar dry hospital environments44
. To simulate the use of
graphene wireless sensors in hospital sanitation and biohazard monitoring, we interfaced the
nanosensors with an intravenous (IV) bag (Fig. 2.11a). Next, 1 µL solutions containing various
concentrations (103-10
8 CFU/mL) of bacterial cells were allowed to dry on the sensor surface for
30 min. Figure 2.11b plots the bandwidth of the sensor corresponding to the different
concentrations of S. aureus cells incubated on the sensor surface. The percentage change in
graphene resistance is depicted in Figure 2.11c; significantly, wireless detection limits of 1
bacterium/µL were achievable in wireless operation mode. The change in graphene resistance
upon bacterial binding was wirelessly monitored as the bandwidth change in the sensor
resonance curve10
.
55
56
Figure 2.11 Wireless monitoring of S. aureus. (a) Optical image of the graphene wireless sensor
integrated ontothe surface of an IV bag. Scale bar is 1 cm. (b) Bandwidth of the sensor resonance
corresponding to various concentrations of S. aureus cells incubated on the sensor surface and
dried. (c) Percentage change in graphene resistance versus concentration of S. aureus. Error bars
show standard deviation (N = 3).
The stability of sensor on the IV bag was tested against mechanical stress associated
with bag crumpling by measuring the change in sheet resistance and transmittance of the
graphene (Fig. 2.12).
Figure 2.12 Structural integrity testing of sensor integrated onto IV bag. Optical images of (a)
IV bag sensor before testing, (b) Immersion of the IV bag sensor in water, (c) Structurally stable
57
sensor after recovery from water. Change in sheet resistance (d) and transmittance (e) of
graphene transducer after undergoing 3 cycles of harsh Q-tip rubbing. Scale bars are 1 cm.
2.3.6 Tooth Platform Monitoring of Breath and Saliva.
To investigate the performance of the sensor when directly integrated with biological tissue, the
sensor was biotransferred onto the surface of a bovine tooth (Fig. 2.13a). Teeth are in constant
contact with breath and saliva, which represent rich biologic media that can be probed for the
presence of disease, infectious agents, or metabolic changes45-47
. Monitoring dynamic
characteristics of respiration, including the presence of biomarkers and volatile organic
compounds (VOCs) in exhaled breath, is of growing interest in non-invasive disease diagnosis46-
48. Significantly, integration of the tooth sensor enabled remote monitoring of breath when
exhaling on the tooth. Figure 2.13b depicts the real-time change in graphene conductance on
exposure to breath. Importantly, the sensor shows rapid response to breath, and the signal was
observed to terminate quickly after the breath pulse.
58
Figure 2.13 Tooth sensor monitoring of breath and saliva. (a) Optical image of the graphene
wireless sensor biotransferred onto the surface of a tooth. Scale bar is 1 cm. (b) Electrical
conductance versus time upon exposure of the sensor to pulses of exhaled breath (red line).
Baseline conductance is shown as blue line (c) Percentage change in graphene resistance versus
time following exposure to ~100 H. pylori cells in human saliva (red line). The response to
“blank” saliva solution is shown as blue line (d) Percentage change in graphene resistance versus
concentration of H. pylori. Error bars show standard deviation (N = 3).
59
Next, we explored the response of the tooth sensors to Helicobacter pylori, a Gram-
negative pathogen found in the stomach and saliva which is estimated to be responsible for the
development of over 90% of duodenal ulcers and stomach cancers49,50
. In particular, we
investigated the ability of the graphene-AMP sensors to selectively recognize H. pylori cells in
human saliva. Tooth sensors were first exposed to a solution of saliva and the signal was allowed
to stabilize. Next, H. pylori cells dissolved in a pooled sample of saliva were allowed to come
into contact with the tooth sensor. Optical experiments with fluorescently labeled bacterial cells
verified that the immobilized AMPs recognize and bind bacterial cells, after incubating in saliva
for ca. 15 min.
Figure 6c depicts the real-time change in graphene resistance on exposure to a 1 µL
sample of human saliva containing ~100 H. pylori cells, while 1 µL of “blank” saliva solution
without any bacterial cells was used as a control. Figure 2.13d thus depicts the percentage
change in resistance as a function of bacterial concentration after 10 minutes by wirelessly
recording the characteristic frequencies at resonance25,51,52
(Methods). A linear relationship was
observed between the logarithm of bacteria concentration and the resistance change up to a
concentration of 106 bacterial cells, with a lower detection limit of ~100 cells. Promisingly, this
latter value is two orders of magnitude less than the minimum infective dose for H. pylori42
. This
demonstrates the natural specificity possessed by AMPs in recognizing and binding to
pathogenic bacterial cells, even in the presence of complex saliva interferrents such as epithelial
cells, proteins, and immunoglobulins.
60
2.3.7 Discussion
This work realizes the direct integration of highly sensitive and selective graphene nanosensors
with natural biomaterials for single cell detection, and for passive, wireless monitoring. The
sensor is realized via the synergistic, hierarchical integration of a variety of smart material
properties. The surface-dominated graphene sensing elements allow for intimate, robust
conformability onto biological tissues or teeth. As a sensing system, the resulting device has
several key meritorious properties, including 1) extremely high sensitivity due to the graphene
network, 2) biotransferability offered by the water-soluble silk fibroin platform, 3) broadly
selective biorecogniton enabled by robust and naturally occurring AMPs, and 4) the ability to
achieve battery-free, wireless remote query operation via the incorporation of a parallel resonant
circuit with a gold thin film patterned meander line inductor53,54
and interdigitated capacitive
electrodes.
Silk thin films serve as an ideal “temporary tattoo” platform due to their optical
transparency, mechanical robustness, biotransferability, flexibility and biocompatibility22,23
.
When crystallized in air, the silk fibroin secondary structure kinetically favors silk I formation, a
disordered collection of -helices and random coils resulting in aqueous solubility. Such films
possess programmable solubility rates dependent on -sheet content and fibroin concentration,
making them ideal substrates for the clean and controlled transfer of graphene to biological and
material surfaces.
Functionalization of graphene nanosensors with bifunctional peptides enables efficient
recognition of pathogenic bacteria. Previous results showed that graphene-binding peptides
display high surface coverage and strong binding activity due to -stacking interactions between
aromatic residues27
. Graphene sheets functionalized with OHP, an AMP isolated from the skin of
61
the frog species Odorrana grahami, enabled broadband detection of Gram-positive and Gram-
negative bacteria. Previous studies showed that bacterial binding of AMPs are observed as a
precursor to bacteriocidal activity32
, and OHP displays broad activity against: H. pylori, a Gram-
negative species found in the stomach and saliva which is responsible for ulcers and stomach
cancers; E. coli, a Gram-negative species found in the lower intestine of endotherms with known
strains capable of acute food poisoning and urinary tract infections resulting from unhygienic
meat and dairy preparation; and S. aureus, a Gram-positive species found on skin flora and
hospital equipment which is notoriously drug-resistant. OHP is also known to exert antimicrobial
activity against methicillin resistant strains of S. aureus (MRSA)41
.
A single layer thin film inductor-capacitor (LC) resonant circuit integrated in parallel
with the resistive graphene monolayer enables wireless readout and battery-free operation. The
change in conductance of the graphene nanosensor on binding of pathogenic bacteria is resolved
from changes in the characteristic frequencies and bandwidth of sensor resonance. Both the
characteristic frequencies and the bandwidth are quantities that are dominatingly determined by
the resonant circuit and readout can thus be insensitive to the mutual inductance (coupling
coefficient) between the sensor and reader coil. Therefore, the relative alignment and location of
the sensor with respect to the reader antenna is unimportant and flexible operation is achieved.
However, we note that improvements in sensor performance will require better control over
potential non-uniformities in analyte coverage, and a reduction of artifacts such as air bubbles in
the case of immersion in liquid.
62
2.4 Materials & Methods
2.4.1 Reagents and Biologicals
The bifunctional peptide GBP-OHP (HSSYWYAFNNKT-GGG
GLLRASSVWGRKYYVDLAGCAKA) containing a graphene binding motif linked to the
antimicrobial peptide odorranin-HP via a triglycine linker were chemically synthesized and
obtained from Peptide 2.0 Inc (Chantilly, VA). Heat-killed pathogenic Gram-negative bacterial
cells of E. coli O157:H7 and H. pylori were purchased from KPL (Gaithersburg, MD). Heat-
killed Gram-positive bacterial cells of S. aureus were purchased from Invitrogen Inc. The human
saliva sample was purchased from Lee Biosolutions (St Louis, MO). The stock solution of
peptide was prepared by reconstitution of the lyophilized powder in DI water. Different
concentrations of bacterial samples were prepared from stock solutions via dilution in deionized
water or human saliva. Phosphate buffered saline consisting of 137 mM NaCl, 2.7 mM KCl, 4.4
mM Na2HPO4 and 1.4 mM KH2PO4 (pH 7.4), FeCl3, sodium carbonate and lithium bromide for
the processing of silk were purchased from Sigma Aldrich (St. Louis, MO).
2.4.2 Preparation of Silk Films.
Bombyx mori cocoons were boiled in 0.02 M Na2CO3 for 30 minutes followed by thorough
rinsing with water. The degummed silk was then dissolved in 9.3 M aqueous lithium bromide
and the solution was dialyzed to remove excess salt. The resulting aqueous solutions were 6-10%
(w/v) fibroin and were preserved by storage at 5 °C. Silk films were made by casting fibroin
solutions onto PDMS and drying in air for 12-24 h, depending on the thickness. When
crystallized in air, silk fibroin secondary structure kinetically favors silk I formation and ca. 50
63
µm thick films. For the preparation of fluorescent silk films for silk dissolution test, silk fibroin
solution was mixed with fluorescence dye and allowed to crystallize overnight.
2.4.3 Fabrication of Graphene/Silk Sensors
CVD grown graphene monolayers from Ni thin films were released and transferred onto
PDMS stamps by removal of the Ni layer in FeCl3. Graphene was then transfer printed onto the
silk films. Clean transfer of graphene onto silk was achieved via moistening of the silk surface
using a wet cotton swab. Planar inductive and capacitive elements were then incorporated onto
the graphene/silk samples to enable wireless interrogation. A meander line design for the
inductive element was deposited on the graphene nanosensor via shadow mask assisted electron
beam evaporation of gold (150-200 nm).
2.4.4 Biotransfer onto Biomaterials
Integration of the sensor onto biomaterial surfaces was achieved via dissolution of the
supporting silk substrate. In the case of dry surfaces such as a tooth, a moistened cotton swab
was used to slightly wet the surface. The graphene-Au electrode sensing elements on the
temporary silk films were then carefully aligned and placed on the tooth surface with the device
side facing down. The temporary silk film platform was gradually dissolved off by application of
water, leaving the ultra-thin sensors intimately attached to the surface by van der Waals forces.
In the case of wet surfaces such as muscle tissue, dissolution of the silk film was faster. IV bags
(Baxter ViaFlex) used for the study were provided by the Princeton University Medical Center.
2.4.5 Graphene Functionalization with AMPs
64
The bifunctional peptide GBP-OHP was dissolved in DI water at a concentration of 1 mg/mL. 5
µL of the peptide solution was dropped onto the graphene and incubated for 15 min, followed by
washing with deionized water and drying.
2.4.6. Single Bacterium Detection Measurements
Electrical measurements for the detection of a single bacterium were performed with a lock-in
detection system using Stanford Research Systems 810 DSP lock-in amplifier. A signal of 50
mV was used with a modulation frequency of 30-70 Hz with zero DC bias to avoid
electrochemical reactions. The resistance of the graphene sensor was monitored continuously in
the presence of analyte samples of various dilutions of bacterial cells. Bacterial cells for optical
monitoring and for antimicrobial peptide-bacteria binding density studies were fluorescently
labeled with propidium iodide in a manner similar to previous studies30
. Stock solutions of
propidium iodide (PI), nucleic acid stain (Molecular Probes, Eugene, OR) were made from solid
form by dissolving PI (MW = 668.4) in deionized water at 1 mg/mL (1.5 mM) and stored at 4 ºC,
protected from light. Heat-killed bacterial cells rehydrated in PBS were then incubated with 3
µM solution of PI (made by diluting the 1 mg/mL stock solution 1:500 in buffer) for 10-15 min.
After incubation, the cells were pelleted by centrifugation and removal of the supernatant, and
were resuspended in DI water or 1×PBS buffer. The binding pattern of the different bacterial
cells was imaged using a Zeiss Axiovert inverted microscope and recorded with a Zeiss
AxioCam digital camera. For real-time detection of bacterial cells (E. coli O157: H7), a 1 µL
sample containing 100 bacterial cells was pipetted onto the graphene sensors. Simultaneous
bright field and fluorescent data were recorded together with lock-in resistance data, with the
focal plane set on the graphene surface to identify the events when the bacterial cells came close
65
to the sensor. The motion of the bacterial cells was tracked with the help of video spot tracker, a
custom automated tracking software (freely available at http://cismm.org/downloads/), and the
manual tracking plugin of the National Institutes of Health’s ImageJ software.
2.4.7 Wireless sensing experiments
A single-layer inductive-capacitive (LC) resonant circuit, integrated in parallel with the resistive
(R) graphene monolayer, formed the basis of the wireless readout unit. The reader device
consisted of a two-turn coil antenna connected to a frequency response analyzer (HP 4191A RF
impedance analyzer). The wireless reader, which was powered by an alternating current source,
was responsible for wirelessly transmitting power and receiving sensor data from the remote
passive sensor, all via inductive coupling (Fig. 2.14).
Figure 2.14 Impedance spectrum of the reader coil. The impedance spectrum of the reader coil
antenna in the presence and absence of the sensing element.
66
The equivalent circuit of the graphene nanosensor reader device is illustrated in Figure
2.17. The sensing element is modeled as an LRC circuit where L is the inductance of the meander
line inductor, C is the capacitance of the graphene/interdigitated electrode capacitive system and
R is the resistance of the graphene transducing element. The reader system for the wireless
measurement consists of a coil antenna connected to a radio frequency impedance analyzer
(Hewlett-Packard 4191A). The reader antenna is used to inductively couple and power the
remote sensing element. The reader coil is excited by an AC voltage signal generated by the
regulated voltage source in the impedance analyzer, and the corresponding current response is
measured as the frequency is varied. The AC sinusoidal signal on the reader coil will result in a
magnetic field in its vicinity, which is calculated based on Faraday’s law55
:
√
where H is the magnetic field intensity, I is the current through the reader coil, r is the radius of
the reader coil (circular coil), N is the number of turns of the coil, and x is the separation between
the reader and the sensor inductors along the central axis. The impedance analyzer is used to
continuously monitor the complex impedance spectrum of the reader-sensor system. In the
absence of the sensing element the impedance spectrum consists of the impedance of the reader
coil antenna alone (Figure 2.14). In the presence of the sensing element, the additional
impedance of the sensor resonant circuit is reflected on the measured complex impedance. The
expression for the complex impedance of the inductively coupled reader-sensor system can be
derived using linear circuit theory and is described elsewhere56
. The bandwidth of resonance is
measured between the half-power (-3dB) points (Figure 2.15). The characteristic frequencies of
67
sensor resonance (resonance frequency and zero reactance frequency) are monitored from the
complex impedance spectrum (Figure 2.16).
Passing an AC signal through the antenna generated a magnetic field, inducing current
via mutual inductance in the coil of the sensing element (Faraday’s law), and finally resulting in
a potential drop that depended on the conductance of the graphene nanosensor. Any change in
the conductivity of the sensor system – resulting from biological or chemical changes occurring
at the transducer surface – was reflected as a change in the frequency characteristics (namely
bandwidth) around the resonance point25,51,57
. This allowed the reader to wirelessly interrogate
the sensing element by measuring the complex impedance of the system. The change in the
capacitance (C), of the graphene-interdigitated electrode sensing system was deduced from the
resonance frequency shift (f), the expression for which is
(1)
√
The bandwidth of the sensor’s resonant-network (B) was measured from the magnitude of the
sensor impedance and used to calculate the change in resistance (R) of the graphene-electrode
sensing element on binding of the bacterial cells (Figure 2.15). The expression for the change in
resistance of the system is
(2) ⁄
68
Figure 2.15 Impedance spectrum of the sensing element. The impedance magnitude of the
sensing element as a function of frequency, illustrating measurement of the resonance bandwidth
from the half-power points.
Frequency measurements on the sensor system were performed by monitoring the complex
impedance spectrum of the system (Figure 2.16).
69
Figure 2.16 Complex impedance spectrum of the sensing element. The complex impedance of
the sensing element as a function of frequency, showing impedance magnitude, real part and
imaginary part. The measurement of the characteristic frequencies of resonance is illustrated.
The frequency at which the imaginary part of the sensor impedance vanishes (fz) was continually
monitored and used to calculate the graphene resistance:
(3) (
)
⁄
where, L is the inductance of the system and can be measured separately. The equivalent circuit
of the sensing element was used to calculate the bandwidth of the reader-sensor system, and the
input impedance of the system was viewed by the reader device (Figure 2.17).
70
Figure 2.17 Electrical equivalent circuit of the graphene based wireless sensing element-reader
system. The graphene based wireless sensing element is modeled as an LRC resonant circuit.
The reader system consists of a coil antenna connected to a radio frequency (RF) impedance
analyzer58
.
2.5 Conclusion
In conclusion, direct integration of highly sensitive graphene nanosensors with biomaterials such
as tooth enamel has enabled battery-free sensors for remote monitoring of pathogenic bacteria.
This work thus represents a fundamentally new paradigm in biochemical detection, and may
provide an in situ, first order monitoring and detection system for applications including point-
of-care diagnostics, hospital sanitation monitoring, and food safety analysis. Yet, these results
are only a prototype, ‘first generation’ platform for interfaced graphene nanosensors. Due to the
semi-selective nature of the interaction of AMPs with pathogenic bacteria, differentiation of
multiple species of pathogenic bacteria has not been achieved. Future work will involve
exploring strategies to improve this selectivity via investigations into multi-ligand59,60
and
aptamer based capture agents26,61
; and antibody based biorecognition molecules with improved
71
stability62
to provide stringent discrimination between species of pathogenic bacteria. Alternative
strategies for covalent and non-covalent functionalization of graphene sensors will also be
explored63
. Finally, future challenges in the sensor development will involve further
miniaturization of the wireless coil for integration onto a smaller footprint (such as a human
tooth)64,65
and testing of the platform on in vivo systems, including tissue and teeth in living
animals and humans.
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79
Chapter 3
Antimicrobial Peptides as Molecular Probes
on Bionic Sensors§
3.1 Overview
The development of a robust and portable biosensor for the detection of pathogenic bacteria
could impact areas ranging from water quality monitoring to testing of pharmaceutical products
for bacterial contamination. Of particular interest are detectors which combine the natural
specificity of biological recognition with sensitive, label-free sensors providing electronic read-
out. Evolution has tailored antimicrobial peptides to exhibit broad-spectrum activity against
pathogenic bacteria, while retaining a high degree of robustness. Here, we report selective and
sensitive detection of infectious agents via electronic detection based on antimicrobial peptide-
functionalized microcapacitive electrode arrays. The semi-selective antimicrobial peptide
Magainin I – which occurs naturally on the skin of African clawed frogs – was immobilized on
gold microelectrodes via a C-terminal cysteine residue. Significantly, exposing the sensor to
various concentrations of pathogenic E. coli revealed detection limits of approximately 1
bacterium/µL, a clinically useful detection range. The peptide-microcapacitive hybrid device was
further able to demonstrate both Gram-selective detection as well as inter-bacterial strain
§ The work reported in this chapter is based on the following original publication: Mannoor, M. S.; Zhang, S.; Link,
A. J.; McAlpine, M. C., Electrical detection of pathogenic bacteria via immobilized antimicrobial peptides.
Proceedings of the National Academy of Sciences of the United States of America, 107 (45), 19207-19212 (2010).
80
differentiation, while maintaining recognition capabilities toward pathogenic strains of E. coli
and Salmonella. Lastly, we report a simulated “water-sampling” chip, consisting of a
microfluidic flow cell integrated onto the hybrid sensor, which demonstrates real-time on-chip
monitoring of the interaction of E. coli cells with the antimicrobial peptides. The combination of
robust, evolutionarily tailored peptides with electronic readout monitoring electrodes may open
exciting avenues in both fundamental studies of the interactions of bacteria with antimicrobial
peptides, as well as the practical use of these devices as portable pathogen detectors.
3.2 Introduction
Bacterial infections remain the leading cause of death in developing nations, accounting for an
estimated 40% of deaths 1. For instance, the strain O157:H7 of E. coli is considered to be one of
the most dangerous food borne pathogens 2,3
. In developed countries, bacterial contamination is
also of critical concern, particularly in the pharmaceutical industry. Indeed, the most reliable test
for contamination is the limulus amebocyte lysate (LAL) test, based on the detection of
endotoxins via coagulation of horseshoe crab blood 4. Microbial infections and drug-resistant
supergerms are also a leading cause of military deaths, particularly in soldiers with burn injuries,
and are considered potential biowarfare agents5-7
. While containment strategies – such as
vaccination and “broadband” antibiotic usage in hospitals – have helped reduce the severity of
bacterial infections, these strategies have also inadvertently promoted the emergence of antibiotic
resistance. Thus, the development of a sensor that can detect the presence of an infectious
outbreak from a broad spectrum of pathogenic species would be highly desirable.
Current methods for detecting pathogenic bacteria include enzyme-linked immunoassay
(ELISA), and polymerase chain reaction (PCR) 8,9
. In the former case, the assays exploit
81
antibodies as molecular recognition elements due to their highly specific targeting of antigenic
sites. However, antibodies lack the stability needed to detect pathogenic species under harsh
environments, reducing the shelf-life of antibody functionalized sensors. The high specificity of
antibody-antigen interactions also requires a one-to-one pairing of antibody-based sensors for
each target to be detected. Nucleic acid probe-based techniques such as PCR can reach single-
cell detection limits, yet require the extraction of nucleic acids and are limited in portability.
By contrast, the ease of synthesis and intrinsic stability of antimicrobial peptides (AMPs)
render them particularly interesting candidates for use as molecular recognition elements in
electronic biosensing platforms10,11
. AMPs appear in multiple niches in nature including the skin
of higher organisms and the extracellular milieu of bacteria as the primary line of defense against
bacteria and fungi12
. AMPs are much more stable than typical globular proteins – explaining how
they can be continually exposed to the natural environment – and are exceptionally efficient at
fending off bacterial infection13
. Indeed, some cationic antimicrobial peptides have shown
activity towards pathogenic bacteria under harsh environmental conditions such as thermal
(boiling/autoclaving) and chemical denaturants14,15
. The replacement of current antibody based
affinity probes with more stable and durable AMPs in biological sensors may thus help to
increase the shelf-life of current diagnostic platforms. Lastly, a major potential advantage of
AMPs as recognition elements stems from their semi-selective binding nature to target cells,
affording each peptide the ability to bind a variety of pathogenic cells.
The bioactivity of AMPs towards microbial cells is classified into groups according to
their secondary structures12
. Many AMPs adopt amphipathic conformations which spatially
cluster hydrophobic from cationic amino acids, thereby targeting the negatively charged head
groups of lipids in the bacterial membrane. In contrast, the membranes of plants and animals
82
seclude negative charges to the inner leaflet, and contain cholesterols which reduce AMP activity
11. By aiming at the very foundation of the bacterial cell membrane, and remaining generically
unrecognizable to proteases 16
, AMPs as antibiotics have remained remarkably free of acquired
resistance. Among AMPs, linear cationic peptides such as magainins are particularly attractive
for microbial sensing applications because of their small molecular size and intrinsic stability
17,18. In particular, the positively charged AMP Magainin I
(GIGKFLHSAGKFGKAFVGEIMKS) binds most selectively to the bacterial cell E. coli
O157:H7 as a precursor to bactericidal activity 19
. Magainin I also displays broad spectrum
activity toward other Gram-negative bacteria, which comprise the majority of pathogenic
infection in humans.
A number of methods have been successful at detecting bacteria including
nanomechanical cantilever sensing (NEMS) 20,21
, surface-enhanced Raman spectroscopy (SERS)
22, and quartz crystal microbalance based sensors
23. Similarly, recent attempts have utilized
AMPs as biorecognition elements in fluorescent-based microbial detection with achievable
detection limits of 5 × 104
cells/mL 24,25
. Yet, the development of an “all-in-one” solution which
combines a high degree of portability, robustness, sensitivity, and selectivity toward pathogenic
strains remains challenging. Among the various label-free signal transduction platforms that have
been investigated, impedance spectroscopy is promising due to its simple instrumentation, ease
of device assembly, and adaptability to multiplexed lab-on-a-chip applications 26,27
. A
microcapacitive sensor detects impedance changes in the dielectric properties of an electrode
surface upon analyte binding, where the variation in the impedance is directly proportional to the
activity of analyte binding 28
. Here, we report for the first time a label-free electronic biosensor
based on the hybridization of the antimicrobial peptide Magainin I with interdigitated
83
microelectrode arrays for the sensitive and selective detection of pathogenic bacteria via
impedance spectroscopy. We anticipate that the combination of compact, naturally bioselective
AMPs with microcapacitive sensors may represent a highly robust and portable platform for
fundamental studies of AMP-bacteria interactions, and for portable infectious disease threat
agent signaling.
3.3 Antimicrobial Peptide based Sensitive Detection of Bacteria
As a first step toward the development of an AMP-based label-free, electronic biosensor, the
targeting of microbial cells by Magainin I was investigated using impedance spectroscopy.
Figure 3.1 schematically outlines our sensing platform.
Figure 3.1 AMP-based electrical detection of bacteria. a) Schematic of AMPs immobilized on
an interdigitated microelectrode array, b) Magnified image of the AMP Magainin I in helical
form, modified with a terminal cysteine residue, and with clearly defined hydrophobic and
hydrophilic faces, c) Detection of bacteria is achieved via binding of target cells to the
84
immobilized AMPs, d) Optical image of the interdigitated microelectrode array (Scale bar: 50
µm).
AMPs are first immobilized on microfabricated interdigitated gold electrodes (Fig. 3.1a;
Materials and Methods). Magainin I was acquired with an additional cysteine residue at the C-
terminus (Fig. 3.1b), allowing for facile and site specific covalent attachment to the gold
electrodes. Next, heat-killed bacterial cells were injected and incubated with the AMP-modified
electrodes. If the bacteria are recognized by the AMPs, binding will occur (Fig. 3.1c), leading to
dielectric property changes which can be monitored by a spectrum analyzer. Sensitivity of
microbial detection is a key determinant for utility of sensors. To this end, the sensitivity of the
magainin-functionalized microelectrode array in detecting bacterial cells was first investigated
using impedance spectroscopy. Figure 3.2 shows the results of measurements performed after
incubation of the immobilized AMPs with pathogenic E. coli O157:H7 cells in concentrations
ranging from 103
to 107 CFU/mL.
85
Figure 3.2 Sensitivity of the AMP electronic biosensor. a) Impedance spectra of various
concentrations of E. coli O157:H7 cells (red), of a non-labeled sensor (blue), and of a sensor
with an N-terminal immobilized AMP (purple), b) Impedance spectra of various concentrations
of E. coli with the AMP sensor at 10 Hz. Error bars show standard deviation (N = 3).
86
A “blank” device with no immobilized AMPs was also tested for comparison; the
impedance of the “blank” device without immobilized AMPs is found to change negligibly upon
exposure to various bacterial concentrations (Fig. 3.3).
Figure 3.3 Impedance spectra of various concentrations of E. coli O157:H7 cells after exposure
to a non-labeled “blank” sensor. The inset shows the optical micrograph of the bare sensor after
exposure to E. coli cells of concentration 107 CFU/mL.
Figure 3.2a shows that at low frequencies, the different concentrations of bacterial cells
have the effect of increasing the impedance in proportion to the number of cells present in the
sample for concentrations greater than 102
CFU/mL. As the frequency increases, the contribution
to the impedance from the bacterial cells decreases, leaving only the dielectric relaxation of
small dipoles including water molecules in the buffer solution to affect the measured impedance.
Figure 3.2b thus depicts the impedance change at a fixed frequency of 10 Hz. The variation in
the impedance is directly proportional to the number of bacterial cells bound to the immobilized
AMPs, and manifested in a logarithmic increase with respect to serially diluted bacterial
concentrations. Significantly, the detection limit of response of the hybrid AMP-microelectrode
87
device to E. coli was found to be 103 CFU/mL (1 bacteria/µL), which compares favorably to the
LAL test29
. This lowest limit of detection appears to be limited by the presence of impedance
due to the electrical double layer resulting from the electrode polarization effect at low
frequencies. Importantly, this sensitivity limit is clinically relevant 30
and compares favorably to
AMP based fluorescent assays [5 × 104 CFU/mL
25] and to antibody-based impedance sensors
26.
To gain further insight into the activity of Magainin I towards E. coli, AMPs were
immobilized “upside-down” via incorporation of a cysteine residue at the N-terminus. The
binding affinities of Magainin I immobilized via cysteine residues at the C-terminus and N-
terminus were compared and co-plotted in Figs. 3.2a and 3.2b. Considerably reduced binding
activity was observed for magainin immobilized via the N-terminus compared to C-terminal
immobilization. This reduction in the binding affinity is likely due to the diminished exposure of
the target bacteria to the amine-containing residues near the N-terminus. This observation
supports the hypothesis that the initial interaction of α-helical AMPs with the membranes of the
target bacteria occurs via electrostatic attraction of positively charged amino acids on the AMP
with negatively charged phospholipids in the bacterial membrane 19,31,32
. Indeed, it has been
previously shown that amino acid omissions in the N-terminal region of magainin result in the
complete loss of antimicrobial activity, whereas analogs with omissions in the C-terminal region
exhibited equal or increased activity 33
.
3.4 Effect of AMP Immobilization Density
Finally, the effect of varying the surface density of the immobilized AMPs on the detection of
bacterial cells was investigated (Fig. 3.4). The response of the biosensor towards target cells was
found to increase monotonically with increasing concentration of immobilized magainin. The
88
effect of varying the surface density of the immobilized AMPs on the detection of bacterial cells
was investigated. Different concentrations of C-terminal cysteine labeled Magainin I were
immobilized on the electrode surface. The impedance response resulting from binding of
pathogenic E. coli O157:H7 cells (107 CFU/mL) to different densities of immobilized AMPs
were recorded. The response of the sensor at 10 Hz is plotted in Figure S3. The immobilized
peptide film was also analyzed via fluorescent microscopy by labeling the peptides with
fluorescein isothiocyanate (FITC) 34
. The ability to capture the target bacteria was found to be
strongly dependent on the immobilization density of the magainin on the sensor surface. This
supports the hypothesis that the initial interaction between the cationic AMPs and the target
species occurs through electrostatic interaction 19,31
. This also suggests that the minimization of
diffusion and steric hindrance which usually affect the binding kinetics do not play a significant
role in the immobilized AMP-bacteria interactions.
Figure 3.4 The effect of the surface density of immobilized Magainin I on the binding of
bacterial cells. Scale bar is 20 µm. Error bars show standard deviation (N = 3).
89
3.5 Selectivity Measurements
As a next step, we investigated the selectivity of the AMP-functionalized biosensors toward
various bacterial species. Specifically, the binding behavior of AMPs was probed toward: 1)
gram-negative pathogenic E. coli O157:H7, 2) the non-pathogenic E. coli strain ATCC 35218, 3)
gram-negative pathogenic Salmonella typhimurium, and 4) Listeria monocytogenes, a gram-
positive pathogen. Collectively, these studies elucidate the matrix of selectivity as it depends on
gram-negative vs. gram-positive species, and pathogenic vs. non-pathogenic strains. The
selectivity was first investigated using fluorescent microscopy methods, by staining bacterial
cells and optically mapping their binding density to gold films hybridized with AMPs. Figure 3.5
shows the discriminative binding pattern of immobilized Magainin I to various bacterial cells (all
107 CFU/mL) stained with propidium iodide (PI) nucleic acid stain (see Methods), as well as the
surface density of the bound bacterial cells.
90
Figure 3.5 Optical microscopy of the selectivity of AMPs. (Left panels) Demonstration of
selective binding of the immobilized AMP to various stained bacterial cells (107 CFU/mL),
including a) E. coli O157:H7, b) Salmonella typhimurium, c) E. coli ATCC 35218, and d)
91
Listeria monocytogenes. (Right panels) The corresponding surface densities of bound cells. Scale
bars are 10 µm.
Likewise, Figure 3.6a plots the electrical response of the AMP-biosensor against these
various species as a function of the interrogating frequency, and Figure 3.6b plots the response at
10 Hz. Intriguingly, inspection of the fluorescent images and surface density plots agree
qualitatively with the response of the AMP electrical biosensor and reveal the following insights.
First, Magainin I exhibits clear preferential binding toward the pathogenic, gram-negative
species E. coli and Salmonella, relative to the gram-positive species Listeria, with a two order of
magnitude impedance difference at 10 Hz (Fig. 3.6b)35,36
. This selectivity was particularly
enhanced for pathogenic E. coli, which showed a slightly larger response relative to Salmonella.
Next, inter-bacteria strain differentiation between pathogenic and non-pathogenic bacteria is
demonstrated by the ability of the sensor to selectively detect pathogenic E. coli relative to the
non-pathogenic strain, again with a nearly two order of magnitude impedance difference at 10
Hz. Finally, the response of the sensor to all microbial species was larger than the response of the
“blank” biosensor which was not functionalized with AMP.
92
Figure 3.6 Impedance spectroscopy of the selectivity of AMPs. a) Impedance spectra of the
AMP functionalized microelectrode array after interaction with various bacterial samples (107
CFU/mL). b) Impedance changes associated with various bacterial species at 10 Hz. Error bars
show standard deviation (N = 3).
93
The response of the sensor to a mixture of pathogenic E. coli and Listeria with a total
cellular concentration of 107
CFU/mL similarly revealed dominant E. coli binding (Fig. 3.7).
Figure 3.7. Impedance spectra of the sensor after exposure to a mixture of pathogenic E. coli and
Listeria of total cellular concentration 107 CFU/mL, in comparison to the sensor response to E.
coli cells of concentration 107
CFU/mL, 106 CFU/mL and Listeria cells of concentration 10
7
CFU/mL.
94
Interestingly, this preferential binding is mitigated in a highly basic medium (Fig.3.8).
Figure 3.8. Impact of varying pH (at pH -3, 7.4, 9.5) on the impedance response of the sensor at
10 Hz, after exposure to pathogenic (O157∶H7) and nonpathogenic (ATCC35218) E. coli cells of
concentration 107cfu/mL.
The observed specificity differences can be explained by noting that a balance between
electrostatic and hydrophobic interactions is believed to underlie the mechanism of bacterial cell
binding by AMPs 31,37
. In the case of magainin I, the difference in the membrane structures of
gram-negative vs. gram-positive bacteria may account for the differential selectivity 38
. Gram-
negative bacteria possess an outer membrane with negatively charged lipopolysaccharide (LPS)
– the first site of encounter for AMPs – and a thin peptidoglycan layer. In contrast, Gram-
positive bacteria lack the LPS-containing outer membrane, instead possessing a thick
95
peptidoglycan layer and teichoic acids. Further, although both pathogenic and non-pathogenic E.
coli cell walls contain LPS, the LPS of the pathogenic strain includes O-antigens, which are
hydrophilic branched sugar side chains. These O-antigens form the outermost portion of the
polysaccharide chain and are thought to enhance electrostatic and hydrogen bonding 39-41
. This
ability of Magainin I to selectively prefer Gram-negative species, and pathogenic versus non-
pathogenic strains of E. coli, agrees with several other bacteria adhesion studies 19,42-44
. The
effect of pH and ionic strengths on the binding behavior of cationic AMPs is well-known 44,45
.
Under conditions for non-physiological pHs the AMPs were found to lose their prefenrential
binding ability to pathogenic E. coli cells versus non-pathogenic E.coli, when the medium
became highly basic (see supporting information). However, we do not expect this behavior to
influence the performance of the sensor as most of the water quality monitoring experiments are
performed under neutral conditions or under conditions of constant ionic strengths.
3.6 Real-Time Detection
To simulate the use of the AMP microelectrodes in everyday applications, such as direct water
sampling, the biosensor response was investigated in real time, as shown in Figure 3.9.
96
Figure 3.9 Real-time binding of bacteria to AMP biosensors. a) Digital photograph of the
microfluidic flow cell. b) Optical micrograph of the microfluidic channel with an embedded
interdigitated microelectrode array chip. c) Optical image of the embedded microelectrode array
after exposure to 107 CFU/mL bacterial cells for 30 min. d) Real time monitoring of the
interaction of the AMP functionalized sensor (and an unlabeled control chip) with various
concentrations of E. coli cells.
First, a microfluidic cell was bonded to the interdigitated biosensor chip (Fig. 3.9a), such
that the electrodes were perpendicular to the direction of the sample flow (Fig. 3.9b) 46
. Next,
fluid was injected using a syringe pump connected to the inlet port, and allowed to flow through
97
to the outlet port, at a flow rate of 100 µL/min. The flow cell was first flushed with buffer to
establish a baseline. Various dilutions (104 – 10
7 CFU/mL) of pathogenic E. coli cells in PBS
were then injected to the channel at a reduced flow rate of 5 µL/min for 30 min. For example,
Figure 3.9c shows the microelectrode array after exposure to 107 CFU/mL bacterial cells.
Simultaneously, the impedance response was continuously monitored during the sample flow-
through process (Fig. 3.9d). All samples produced a measureable response relative to the control
sample within 5 minutes, with the highest concentration sample yielding a response within 30
seconds; these responses saturated after ca. 20 min. These results bode well for the
implementation of this sensor in continuous monitoring of flowing water supplies. Yet, it should
be noted that for the same concentration of bacterial cells, the response of the sensor under flow-
through conditions was found to be comparatively lower than the response after static incubation.
We attribute this to the opposing effects of shear and mixing on the binding kinetics, as reduced
binding of AMPs to target cells under flow-through conditions has also been reported in
fluorescent based assays 24
.
3.7 Materials and Methods
3.7.1 Antimicrobial Peptides and Bacterial Cells
Antimicrobial peptide Magainin I (GIGKFLHSAGKFGKAFVGEIMKS), chemically
synthesized to contain a C-terminal cysteine residue via standard N-fluorenylmethoxycarbonyl
(FMOC) solid phase peptide synthesis, was obtained from Anaspec (San Jose, CA). Magainin I
was also synthesized with an N-terminal Cysteine to compare the bacterial binding activity.
Heat-killed pathogenic bacterial cells of E. coli O157:H7, Salmonella typhimurium and Listeria
monocytogenes were purchased from KPL (Gaithersburg, MD). Heat-killed cells of a non-
98
pathogenic strain of E-Coli (ATCC 35218) was obtained from American Type Cell Culture
(ATCC, Manassas, VA) for control experiments. The stock solution of AMP was prepared by the
reconstitution of the lyophilized product in phosphate buffered saline (Sigma-Aldrich, St. Louis,
MO) consisting of 137 mM NaCl, 2.7 mM KCl, 4.4 mM Na2HPO4 and JM 1.4 mM KH2PO4 (pH
7.4) 29,44
. The heat-killed bacterial cells were rehydrated in PBS, according to manufacturer
recommendations.
3.7.2 Interdigitated Microelectrode Array (IMA) and Microfluidic Flow Cell
Interdigitated capacitive electrodes were microfabricated on 4” p-type silicon wafers (boron-
doped, <100>, 10-16 Ω-cm, 550 µm thick). A 1 µm thick silicon dioxide layer was deposited on
the wafer by plasma enhanced chemical vapor deposition (PECVD) to form electrical insulation
between the Si substrate and the capacitive electrodes. S1813 photoresist was patterned using
photolithography, followed by electron-beam evaporation of 10 nm Ti and 300 nm Au. The IMA
was then finally developed by lift-off patterning of the metallic layer in acetone with ultrasonic
activation. The electrode array consisted of 50 pairs of interdigitated capacitive electrodes with
an electrode width and separation of 5 µm. A polydimethylsiloxane (PDMS) microfluidic flow
cell consisting of a detection microchamber with an embedded microelectrode array, inlet and
outlet ports was formed by bonding the IMA chip to the PDMS channel. The PDMS micro-
channel formed on the master mold was partially cured, aligned with the microelectrode array
and bonded by permanently curing at 80 ºC for 2-3 hr. Microfluidic connectors were fixed on to
the inlet and outlet ports through drilled holes.
99
3.7.3 Sensor Surface Functionalization with Magainin
A simple technique for the immobilization of peptides to a gold surface is through the utilization
of native thiol groups present in cysteine residues 47-50
, and cysteine residues can be synthetically
introduced at a specific site of the peptide to form a properly oriented recognition layer 49,51-53
.
Previous studies have revealed that the covalent immobilization of AMPs on gold surfaces via C-
terminal cysteine leads to adsorption at an angle to the surface 43,54
. Prior to the immobilization
procedure, the gold IMA electrodes were cleaned using acetone, isopropanol and DI water. Stock
solutions of the AMPs were prepared in phosphate-buffered saline (PBS), pH 7.4, consisting of
137 mM NaCl, 2.7 mM KCl, 4.4 mM Na2HPO4 and 1.4 mM KH2PO4 29,44
. For the
immobilization of the AMPs, 800 µg/ml (unless otherwise mentioned) of Magainin I in PBS
buffer was injected into the sensing chamber and incubated for 60 min under static conditions.
The functionalized electrodes were then rigorously washed with 1×PBS to remove any unbound
AMPs, rinsed with de-ionized water and dried in liquid nitrogen. Gold surfaces covalently
functionalized with magainins have shown antimicrobial binding activity persisting for at least
six months 54
.
3.7.4 Fluorescent Microscopy
Stock solutions of propidium iodide (PI), nucleic acid stain (Molecular probes, Eugene, OR) was
made from solid form by dissolving PI (MW = 668.4) in deionized water at 1 mg/mL (1.5 mM)
and stored at 4ºC, protected from light. Heat-killed bacterial cells rehydrated in PBS were then
incubated with 3 µM solution of propidium iodide, PI (made by diluting the 1 mg/mL stock
solution 1:500 in buffer) for 10-15 min 55
. After incubation, the cells were pelleted by
centrifugation and removal of the supernatant and were re-suspended in fresh 1×PBS buffer. The
100
samples of stained bacterial cells (E. coli O157: H7, Salmonella, non-pathogenic E. coli and
Listeria, all 107CFU/mL) were then allowed to incubate with the immobilized Magainin for 15-
20 min in the dark. After incubation, the Au surfaces were washed with PBS buffer and dried
under liquid nitrogen. The binding pattern of the different bacterial cells was imaged using a
Zeiss axiovert inverted microscope and recorded with a Zeiss axiocam digital camera. Surface
density of the bound bacterial cells was analyzed and plotted using the ImageJ software package.
3.8 Impedance Spectroscopy Measurement Details
Dielectric property changes due to AMP-bacteria interactions were probed using a Fast-Fourier
Transform (FFT) spectrum analyzer. The dielectric properties were investigated over a frequency
range of 10 Hz to 100 kHz, with 0 V DC bias and 50 mV AC signals using a SRS 785, 2-channel
dynamic signal analyzer. An in-house LabView program routine was used to collect and record
the data through a GPIB interface. An external op-amp amplifier circuit was used to minimize
the noise and a MATLAB program was used to plot the impedance spectra from the analyzer
output (Fig. 3.9). For sensitivity measurements, pathogenic gram-negative E. coli O157:H7
bacterial cells were injected into the microfluidic flow channel at various dilutions, and
incubated with the immobilized magainins for 12-15 min, under static conditions. To ensure the
response of the sensor toward bound bacterial cells, the impedance spectrum was taken after the
removal of unbound cells by thorough washing in PBS. For real-time measurements, the
impedance vs. time data was recorded while buffer solutions or different dilutions of bacterial
solutions flowed through the microfluidic channel. The flow cell was first flushed with 1x PBS
buffer at a flow rate of 100 µL/min to establish a baseline. Bacterial detection measurements
were performed with the sample flowing at a rate of 5 µL/min. The sensor device was
101
regenerated via a cleaning solution containing 1 M NaCl, 100 mM HCl, and 200 mM CHAPS
followed by 1× PBS buffer. The electrodes were then thoroughly flushed with DI water to
remove any salts. The effect of bacterial cells binding to immobilized magainins on the
impedance signal is due to the dielectric property of the cell membrane. All experiments were
repeated three times.
3.8.1 Measurement setup
Figure 3.9a shows a schematic of the measurement setup used. The AC voltage applied to the
electrodes produces both conduction and displacement current through the sample. The real and
imaginary parts of the transfer function are proportional to the conductivity and the
dielectric constant, respectively. The output of the signal analyzer is applied to one of the
capacitive electrodes through R1. The other electrode of the capacitive sensor is connected to the
negative input of the amplifier A2, which holds the electrode at ground potential. As a result, the
current I that flows through the sensor produces a voltage V2 which is equivalent to the product
of I and the sample impedance Z. The value of voltage drop V1 is equal to the product of I and
R2. Thus the transfer function of the system is given by (1),
(1)
where Z is the overall impedance of the sensing system. The purpose of R1 is to provide an upper
limit for the current I as the impedance Z becomes smaller at higher frequencies. The unity gain
amplifier A1 provides buffering so that the input impedance of Channel 2 does not affect the
voltage drop across the sample.
1
2
V
V
21
2
R
Z
V
V
102
3.8.2 Equivalent Circuit
A high density interdigitated microelectrode array was used for the detection of bacterial cells.
Exposure of the magainin functionalized sensor to bacterial cells results in the binding of the
cells on the electrode surface. Binding of bacterial cells causes a change in the impedance
measured across the electrodes. Figure 3.9b shows an equivalent circuit of the microelectrode
solution interface before the binding bacterial cells. CDL represents the capacitance due to the
electrical double layer between the electrode and the buffer solution, CDi represents the dielectric
capacitance, and RBuffer the bulk resistance of the buffer solution 56
. A parasitic capacitance from
the oxide layer between silicon and gold is shown as CPAR. Figure 3.9c shows a simplified circuit
diagram of the system after bacterial binding to the AMP functionalized electrodes. The
modification in the interface impedance due to the bacterial impedance consists mainly of the
capacitance of the cell membrane CCM, the resistance of the membrane RCM, and the resistance of
the cytoplasm RCyt, as shown. The represented model has two parallel branches, a dielectric
capacitance branch and an impedance branch. At high frequencies, the total impedance of the
system Z will be dominated by the dielectric capacitance of the medium, and the contributions
from the electrical double layer capacitance and the bulk medium resistance will be minimized.
At lower frequencies (< 1 MHz), current does not flow through the dielectric capacitance branch,
and the bacterial cells add different impedance components in series with the impedance branch.
103
104
Figure 3.10 a) Schematic of the impedance spectroscopy measurement setup (adapted from
reference 57). b), c) Simplified equivalent circuit of the microelectrode array/electrolyte interface
b) before bacterial binding, and c) after bacterial binding57
.
3.9 Conclusion
In summary, coupling of AMPs with microcapacitive biosensors has resulted in the
implementation of a portable, label-free sensing platform for the detection of infectious agents.
The achievable sensitivity approached 1 bacterium/µL – a clinically relevant limit – and the
AMPs allowed for sufficient selectivity to distinguish pathogenic and gram-negative bacteria,
while retaining broadband detection capabilities. The sensor surface when exposed to a
simulated real life sample, exhibited the ability to selectively bind pathogenic E. coli cells from a
mixture of Gram negative and Gram positive (Listeria) bacterial cells. Finally, real-time sensing
results demonstrated the capability of the relatively simple impedance-based transduction
architecture to directly detect bacteria, suggesting a promising alternative to traditional antibody
based immunoassays. We anticipate these results could provide a significant positive impact on
the use of pathogenic sensors to test and monitor bacteria in reservoir water, or for use as
biological threat agent detection systems. Yet, a number of key challenges remain. First, the
detection of bacteria in real water samples has not yet been studied. Second, although the
selectivity of the magainin functionalized sensors has been demonstrated under specified
conditions, the scenario could be more complex when the concentrations of the target species are
unknown or when there are multiple infectious agents present. Finally, based on previous work
by our group in coupling peptides to silicon nanowire sensors 58,59
, significantly enhanced
sensitivity may be achievable by reducing the sensors down to the nanometer scale.
105
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Chapter 4
3D Printed Bionic Ears§
4.1 Overview
The ability to three-dimensionally interweave biological tissue with functional electronics could
enable the creation of bionic organs possessing enhanced functionalities over their human
counterparts. However, current electronics are inherently two dimensional, preventing seamless
multidimensional integration with biology. Here, we present a novel strategy for overcoming
these difficulties via additive manufacturing of biological cells with electronic and structural
elements. As a proof of concept, we generated a bionic ear via 3D printing of a cell-seeded
hydrogel matrix in the precise anatomic geometry of a human ear, along with an intertwined
conducting polymer consisting of infused silver nanoparticles. This allowed for the in vitro
culturing of cartilage tissue around an inductive coil antenna in the ear, which subsequently
connects to cochlear-like electrodes. The printed ear exhibits enhanced auditory sensing for radio
frequency reception, and complementary left and right ears can listen to stereo audio music.
4.2 Introduction
The design and implementation of bionic organs and devices that enhance human capabilities,
known as cybernetics, has been an area of increasing scientific interest.1-3
This field has the
§ The work reported in this chapter is based on the following original publication: Mannoor M. S., Z. Jiang, T.
James, Y. L. Kong, K. A. Malatesta, W. O. Soboyejo, N. Verma, D. H. Gracias, M. C. McAlpine, 3D Printed Bionic
Ears. Nano Letters 13, 2634-2639 (2013).
113
potential to generate customized replacement parts for the human body, or even create organs
containing capabilities beyond what human biology ordinarily provides. In particular, the
development of approaches for the direct multidimensional integration of functional electronic
components with biological tissue and organs could have tremendous impact in regenerative
medicine, prosthetics, and human-machine interfaces.4,5
Recently, several reports have described
the coupling of electronics and tissues using flexible and/or stretchable planar devices and
sensors that conform to tissue surfaces, enabling applications such as biochemical sensing and
probing of electrical activities on surfaces of the heart,6 lungs,
7 brain,
8 skin
9 and teeth.
10
However, attaining seamless three dimensionally entwined electronic components with
biological tissues and organs is significantly more challenging.4
Tissue engineering is guided by the principle that a variety of cell types can be coaxed
into synthesizing new tissue if they are seeded onto an appropriate three-dimensional hydrogel
scaffold within an accordant growth environment.11-16
Such cell-hydrogel constructs form tissue
structures having the morphology of the original polymer template following in vivo or in vitro
culture.17
However, a major challenge in traditional tissue engineering approaches is the
generation of cell-seeded implants with structures that mimic native tissue, both in anatomic
geometries and intra-tissue cellular distributions.18
Techniques involving seeding cells into pre-
molded scaffolds have been used to demonstrate the fabrication of three dimensional tissues with
complex geometries. Yet, such techniques suffer from issues such as seeding depth limitations
and non-uniform seeding and hence do not offer the ability to easily create parts (organs or
tissue) with required spatial heterogeneities to meet the shortage of donor organs for
transplantation.19,20
For instance, total external ear reconstruction with autogenous cartilage –
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with the goal of re-creating an ear that is similar in appearance to the contralateral auricle –
remains one of the most difficult problems in the field of plastic and reconstructive surgery.21
Additive manufacturing techniques such as 3D printing offer a potential solution via the
ability to rapidly create computer-aided design (CAD) models by slicing them into layers and
building the layers upwards using biological cells as inks, in the precise anatomic geometries of
human organs.22-24
Variations of 3D printing have been used as methods of solid freeform
fabrication, although its use has mainly been limited to the creation of passive mechanical
parts.22,25
Extrusion-based 3D printing has been used to engineer hard tissue scaffolds such as
knee menisci and intervertebral discs complete with encapsulated cells.26
Further, this technique
offers the ability to create spatially heterogeneous multi-material structures by utilizing
deposition tools that can extrude a wide range of materials.27
This could allow for the
simultaneous printing of electronic materials and biological cells to yield three dimensionally
integrated cyborg tissues and organs exhibiting unique capabilities.
4.3 Our Approach
Here we introduce a conceptually new approach that addresses the aforementioned challenges by
fully interweaving functional electronic components with biological tissue via 3D printing of
electronic materials and viable cell-seeded hydrogels in the precise anatomic geometries of
human organs. Since electronic circuitry is at the core of sensory and information processing
devices,28
in vitro culturing of the printed hybrid architecture enables the growth of “cyborg
organs” exhibiting enhanced functionalities over human biology. Our approach offers the ability
to define and create spatially heterogeneous multimaterial constructs by extruding a wide range
of materials in a layer-by-layer process until the final stereolithographic geometry is complete.
This concept of 3D printing of living cells together with electronic components and growing
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them into functional organs represents a new direction in merging electronics with biological
systems. Indeed, such cyborg organs are distinct from either engineered tissue or conformal
planar/flexible electronics and offer a unique way of attaining a three dimensional merger of
electronics with tissue.
4.4 3D Printing of Bionic Ear: Steps
As a proof of concept of this approach, we evaluated the ability of 3D printing to create a viable
ear auricle which also contains electronics that broaden the capabilities of human hearing.
Human organs comprising cartilaginous tissue, such as the ear auricle, represent suitable
prototype candidates to investigate the feasibility of our approach. This is due to 1) the inherent
complexity in the ear’s anatomical geometry, which renders it difficult to bioengineer via
traditional tissue engineering approaches, as well as 2) the simplicity in its tissue level structure
due to the lack of vasculature.21,29
Specifically, we demonstrate 3D printing of a chondrocyte
seeded alginate hydrogel matrix with an electrically conductive silver nanoparticle (AgNP)
infused inductive coil antenna, connecting to cochlear-like electrodes supported on silicone.
Taken together, the result is three dimensional integration of functional electronic components
within the complex and precise anatomic geometry of a human ear (Fig. 4.1).
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Figure 4.1 Three dimensional interweaving of biological tissue and electronics via additive
manufacturing to generate a bionic ear. (a) cad drawing of the bionic ear. (b) (top) various
functional materials, including biological (chondrocyte cells), structural (silicone), and electronic
(agnp-infused silicone) used to form the bionic ear. (bottom) 3d printer used for the printing
process. (c) Illustration of the 3d printed bionic ear.
The following steps are involved in the process. First, a CAD drawing of the bionic ear
(Fig. 4.1a) is used to prescribe the anatomic geometry and the spatial heterogeneity of the
various functional materials. As described above, three materials comprise the three functional
constituents (structural, biological, and electronic) of the bionic ear. These materials are fed into
a syringe extrusion based Fab@Home 3D printer (The NextFab Store, Albuquerque, NM) (Fig.
4.1b). The printed bioelectronic hybrid ear construct is then cultured in vitro to enable cartilage
tissue growth and fusing together to form a “cyborg ear,” with expanded auditory senses of radio
frequency (RF) reception provided by an inductive coil acting as a receiving antenna (Fig. 4.1c).
To demonstrate our approach, we printed the bionic ear construct. For the scaffold, we pre-
seeded an alginate hydrogel matrix with viable chondrocytes at a density of ~60 million cells/mL
(Materials & Methods). Alginate matrix is three dimensionally stable in culture, non-toxic, pre-
seeding and extrusion compatible, and a suitable cell delivery vehicle because crosslinking can
be initiated prior to deposition.30
Chondrocytes used for the printing were isolated from the
articular cartilage of one month old calves (Astarte Biologics, Redmond, WA). A CAD drawing
of a human ear auricle in stereolithography format (STL) with an integrated circular coil antenna
connected to cochlear electrodes was used to define the print paths by slicing the model into
layers of contour and raster fill paths. Crosslinking was initiated in the alginate hydrogel matrix
pre-seeded with viable chondrocytes, which was then 3D printed along with conducting (AgNP-
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infused) and non-conducting silicone solutions. Together, this method produced the biological,
electronic and structural components of the bionic organ in a single process.
4.5 Growth and Viability of the Bionic Ear
Figure 4.2a shows the 3D printed bionic ear immediately after printing. Notably, it is found to
faithfully reproduce the CAD drawing, in the precise material spatiality for each material as
dictated by the design. The printed ear construct was immersed in chondrocyte culture media
containing 10% or 20% fetal bovine serum (FBS), which was refreshed every 1-2 days
(Materials& Methods). The hybrid ear showed good structural integrity and shape retention
under culture (Fig.4.2b). Over time, the construct gradually became more opaque; this was most
apparent after four weeks of culture, and is grossly consistent with developing an extracellular
matrix (ECM)
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Figure 4.2 Growth and viability of the bionic ear. (a) Image of the 3D printed bionic ear
immediately after printing. (b) Image of the 3D printed bionic ear under in vitro culturing. Scale
bars in (a) and (b) are 1 cm. (c) Chondrocyte viability at various stages of the printing process.
Error bars show standard deviation with N=3. (d) Variation in the weight of the printed ear over
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time in culture, where the ear consists of chondrocyte-seeded alginate (red) or only alginate
(blue). Error bars show standard deviation with N=3. (e) Histologic evaluation of chondrocyte
morphology using H&E staining. (f) Safranin O staining of the neocartilaginous tissue after 10
weeks of culture. (g) Photograph (top) and fluorescent (bottom) images showing viability of the
neocartilaginous tissue in contact with the coil antenna. (h) Photograph (top) and fluorescent
(bottom) images of a cross section of the bionic ear showing viability of the internal
cartilaginous tissue in contact with the electrode. Top scale bars are 5 mm; bottom are 50 μm.
4.5.1 Viability of the Printing Process
Viability was tested immediately before and during the various stages of the printing process.
Initial viability of cells was determined after culturing using a Trypan blue cell exclusion assay
(Corning Cellgrow, Mediatech, VA) and was found to be 96.37 ± 1.71% (Fig. 2C) ((Materials&
Methods).). The printed cell-seeded alginate ear was also tested with a LIVE/DEAD® Viability
Assay (Molecular Probes, Eugene, OR) and exhibited a cell viability of 91.26 ± 3.88% with
homogeneous chondrocyte distribution. This result suggests that the printing process, including
cell encapsulation and deposition, does not negatively impact chondrocyte viability.
Notably, this approach of printing a pre-seeded hydrogel matrix eliminates the major
problems associated with seeding depth limitations and non-uniform seeding in traditional
methods for seeding premolded 3D scaffolds. Seeding chondrocytes into a bioabsorbable
alginate matrix and shaping it via 3D printing localizes the cells to a desired geometry, allowing
for new ECM production in defined locations when cultured in nutritive media. As tissue
develops, the polymer scaffold is reabsorbed (Fig. 4.2d), so that new tissue retains the shape of
the polymer in which the cells were seeded. The biodegradable scaffolding provides each cell
with better access to nutrients and more efficient waste removal.
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The gross morphology of the bionic ear after 10 weeks of in vitro culture is shown in
Figure 4.3.
Figure 4.3 Gross morphology of the 3D printed bionic ear after 10 weeks of in vitro culture.
Scale bar is 1 cm.
4.6 Histologic Characterization
Next, histologic evaluation was used to compare the morphology of chondrocytes in the
neocartilage of the bionic ear to that of the native cartilaginous tissue. Hematoxylin and eosin
(H&E) staining revealed uniform distribution of the chondrocytes in the constructs (Fig. 4.2e)
(Materials & Methods). Histology of the of the ear tissue with Safranin O staining indicated
relatively uniform accumulation of proteoglycans in the cultured ear tissue (Fig. 4.2f). These
biochemical data are consistent with the development of new cartilage.31
Finally, fluorescent
measurements were used to ascertain the viability of the 3D printed bionic ear tissue after 10
weeks of in vitro growth culture. Figures 4.2g and 4.2h show the tissue covering the coil antenna
and the internal tissue that is in contact with the electrode that runs perpendicular through the
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tissue, respectively. In both cases, the grown cartilage exhibited excellent morphology and tissue
level viability. Notably, this approach of culturing cells which fuse into tissue in the presence of
abiotic electronic materials could minimize the immune response of the grown tissue.
4.7 Biochemical and Biomechanical Characterization
We then characterized the mechanical properties of the cartilage at various stages of growth, as
ECM development correlates strongly with the developing tissue’s mechanical properties.32
First,
extensive biochemical and histologic characterizations were performed ((Materials& Methods).
Samples were removed from cultures containing 10% and 20% FBS at 2, 4, 6, 8 and 10 weeks
and frozen to measure DNA content of the neocartilage and for biochemical evaluation of the
ECM. ECM accumulation in the constructs was evaluated by quantifying the amount of two
important components of ECM: 1) hydroxyproline (HYP) as a marker of collagen content, and 2)
sulfated glycosaminoglycan (GAG) as a marker of proteoglycans. By week 10, HYP content
increased to 1.24 ± 0.10 μg/mg and 1.43 ± 0.15 μg/mg for cultures containing 10% and 20%
FBS, respectively (Fig. 4.4a). The corresponding values of GAG content for week 10 were 10.63
± 0.56 μg/mg and 12.24 ± 0.98 μg/mg (Fig. 4.4b).This increase in GAG and HYP content
indicates that chondrocytes are alive and metabolically active in culture.
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Figure 4.4 Biomechanical characterization of the 3D printed neocartilage tissue. (a) Variation of
HYP content over time in culture with 20 % (red) and 10 % (blue) FBS. (b) Variation of GAG
content over time in culture with 20 % (red) and 10 % (blue) FBS. (c) Variation of Young’s
modulus of 3D printed dog bone constructs over time in culture with 20 million (blue) and 60
million (red) cells/mL. Error bars for parts a-c show standard deviation with N=3. (d) Various
anatomic sites of the ear auricle, with corresponding hardness listed in Table 1. Scale bar is 1 cm.
4.7.1 Tensile Testing 3D Printed Cartilage Dog bones
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Next, tensile properties were analyzed by testing 3D printed chondrocyte-alginate dogbone
samples at various points in culture, in which the dogbones contained the same cell densities and
identical culturing conditions as the ear (Materials & Methods). Evaluation of the mechanical
properties indicated that the Young’s modulus of the dogbones increased with time from 14.16
kPa to 111.46 kPa at week 10 (Fig. 4.4c). Dogbones of a lower chondrocyte density of 20 million
cells/mL were also tested under similar conditions to understand the effect of the initial
chondrocyte density in the mechanical properties of the grown tissue. These were found to
possess a lower Young’s modulus of 73.26 kPa at week 10.
4.7.2 Hardness Testing of 3D Printed Neocartillage
Next, the hardness of the grown cartilaginous tissue of the 3D printed auricle was characterized
using nanoindentation measurements. The indentations were performed at the various anatomic
sites of the auricle (Fig. 4.4d). As shown in Table 1, these hardness values were found to be
relatively uniform, ranging from 38.50 kPa to 46.80 kPa.33
4.8 Electrical Characterization
To demonstrate the enhanced functionalities of the 3D printed bionic ear, we performed a series
of electrical characterizations. First, the resistivity of the coil antenna was measured using four
point probe measurements and found to be dependent on the volumetric flow rate used for
printing the conducting AgNP-infused silicone (Materials & Methods). At the optimum flow
rate, the resistivity of the printed coil was found to be 1.31 × 10-6
Ω·m, which is only two orders
of magnitude higher than pure silver (1.59 × 10-8
Ω·m). Next, we performed wireless radio
frequency reception experiments. To demonstrate the ability of the bionic ear to receive signals
beyond normal audible signal frequencies (in humans, 20 Hz to 20 kHz), we formed external
connections to the cochlea of the bionic ear (Fig. 4.5a). The ear was then exposed to sine waves
124
of frequencies ranging from 1 MHz to 5 GHz. The S21 (forward transmission coefficient)
parameter of the coil antenna was analyzed using a network analyzer and was found to transmit
signals across this extended frequency spectrum (Fig. 4.5b).
125
Figure 4.5 Electrical characterization of the bionic ear. (a) Image of the experiment used to
characterize the bionic ear. The ear is exposed to a signal from a transmitting loop antenna. The
output signal is collected via connections to two electrodes on the cochlea. Scale bar is 1 cm. (b)
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Response of the bionic ear to radio frequencies in terms of S21, the forward power transmission
coefficient. (c) (top) Schematic representation of the radio signal reception of two
complementary (left and right) bionic ears. (bottom) Photograph of complementary bionic ears
listening to stereophonic audio music. (d) Transmitted (top) and received (bottom) audio signals
of the right (R) and left (L) bionic ears.
4.8.1 Bionic Ears: Listening of Stereo Music
Most importantly, as a demonstrative example of the versatility in modifying the final organ by
modifying the CAD design, we printed a complementary left ear by simply reflecting the original
model (Materials & Methods). Left and right channels of stereophonic audio were exposed to the
left and right bionic ear via transmitting magnetic loop antennas with ferrite cores (Fig. 4.5c).
The signals received by the bionic ears were collected from the signal output of the dual cochlear
electrodes and fed into a digital oscilloscope and played back by a loud speaker for auditory and
visual monitoring. Excerpts of the transmitted and received signals of duration 1 ms for both the
right and left bionic ears are shown in Figure 4.5d and are found to exhibit excellent
reproduction of the audio signal. Significantly, the played back music (Beethoven’s “Für Elise”)
from the signal received by the bionic ears possessed good sound quality.
4.9 Materials and Methods
4.9.1 Chondrocyte Culturing
Chondrocytes isolated from the articular cartilage of one month old calves were obtained from
Astarte Biologics (Redmond, WA). The cells were cultured in Dulbecco’s Modified Eagle
Medium (DMEM) with 10% fetal bovine serum for 6 to 8 days. A 1% antibiotic-antimycotic
solution consisting of 10,000 U/mL penicillin G sodium, 10,000 μg/mL streptomycin sulfate, and
127
25 μg/mL amphotericin B in 0.85% saline was also added to prevent contamination. The cells
were cultured at 37 °C and 5% CO2.34
Once the initial seeding density of the cells was reached,
the viability was determined using a Trypan blue (Corning Cellgrow, Mediatech, VA) cell
exclusion assay. The chondrocytes were diluted in acid azo exclusion medium of the dye into a
1:1 solution of the cell suspension in 0.4% Trypan blue dye. The cells were incubated in the
medium for less than 5 minutes. The nonviable cells that stained blue were then counted under a
microscope and found to be 96.58 ± 1.64%. The chondrocytes were then suspended in phosphate
buffered saline and pelleted by centrifugation.
4.9.2 Alginate Formulation and Chondrocyte Seeding
To make the hydrogel matrix, low-viscosity, high G-content non-medical grade alginate protanal
LF10/60 alginate (FMC Biopolymer, Drammen, Norway) was dissolved at a concentration of 30
mg/mL, removed of clumps by passing through a 0.22 μm filter, and mixed with the cell pellet
by gentle stirring. The alginate-cell suspension was vortexed and mixed in a 2:1 ratio with
autoclaved 5 mg/mL CaSO4 in PBS to achieve the desired final cell seeding density (60 × 106
cells/mL for the printed ears and 20 × 106 cells/mL for comparison of mechanical properties).
4.9.3 3D Printing
A CAD file of the bionic ear in STL format was used to define the print paths by slicing the
model into layers of contour paths and raster fill paths. Each of the functional materials used for
the creation of the bionic ear, including cells, conducting polymers (Silicone Solutions,
Twinsburg, OH), and structural polymers (RTV silicone, 3M, St. Paul, MN) were then loaded
into the deposition tool and printed in the spatial heterogeneity determined by the CAD.
128
The efficiency of the 3D printing process in printing the biological cells was assessed by
comparing the viability of the chondrocytes before and after the printing process. The efficiency
of the 3D printing process in printing the electronic material was characterized by comparing the
resistivity of the printed coil geometry at various volumetric flow rates (Fig. 4.6).
Figure 4.6 Resistivity measurements. (a) Image of the four point probe measurement of
conducting traces of AgNP-infused silicone printed at various volumetric flow rates. (b) Print
efficiency at various volumetric flow rates. Error bars show standard deviation with N=3.
4.9.4 Culturing Conditions
To aid the comparison, ‘print efficiency’ was arbitrarily defined as the ratio of the theoretical
resistivity of the material to the resistivity of the 3D printed material. Resistivity was measured
using a 4 point probe apparatus to negate contact resistance. Print efficiencies for various
printing speeds were calculated and compared to identify the optimum printing conditions.
The 3D printed bionic ear was then cultured in the same medium as above containing
10% or 20% fetal bovine serum (FBS) at 37 °C and 5% CO2 (Figs. 4.7 and 4.8).
129
Figure 4.7 Images of the 3D printed ear auricle cultured in 10% FBS at various stages of growth.
(a) As printed, (b) after 5 weeks in culture, and (c) after 10 weeks in culture. Scale bars are 1 cm.
Figure 4.8 Image of neocartilage growth of the 3D printed ear under culture containing 20%
FBS, showing bulbous outgrowth on the surface as indicated by the arrows. Scale bar is 1 cm.
The chondrocyte to feed medium ratio was kept below 1.7 million cells/mL per day to
ensure sufficient nutritional supply to the cells. To demonstrate the versatility of our approach in
modifying the final organ by modifying the CAD design, we printed a complementary left ear by
130
simply reflecting the original model and following the same culturing conditions as before (Fig.
4.9).
Figure 4.9 Images of the 3D printed left bionic ears at various stages of growth. (a) As printed,
(b) after 6 weeks in culture, and (c) after 10 weeks in culture. Scale bars are 1 cm.
The media after incubation was tested for bacterial contamination with 100 μM BacLight
Green stain (Molecular Probes, Eugene, OR). To verify the effect of the culturing on the
electronic properties of the AgNP-infused conducting silicone, the resistance of the coil antenna
and the cochlear-like electrodes were measured at various points in culture using a 4 point probe
measurement apparatus. The resistance was found to be constant over time in culture, because
the silicone covering the outer surface of the conducting traces forms an insulating and water-
proof coating. This was confirmed via SEM micrographs of the 3D printed conducting traces
(Fig. 4.10).
131
Figure 4.10 Electrical resistance of the coil antenna in culture. (a) SEM image of the coil
antenna surface. Scale bar is 100 µm. (b) Resistance per unit length of the coil antenna over time
in culture. Error bars show standard deviation with N=3.
4.9.5 Cellular and Tissue Viability
The effect of the 3D printing process on the viability of the chondrocytes was analyzed by
measuring the viability before and immediately after the printing process (Fig. 4.11). First, the
viability of the chondrocytes after mixing with the alginate hydrogel was tested with a
LIVE/DEAD® Viability Assay (Molecular Probes, Eugene, OR). The samples were stained with
0.15 μM calcein AM and 2 μM ethidium homodimer-1 (EthD-1) for approximately an hour at
room temperature. The viability of the cells in the printed ear construct was also measured by
taking specimens from various locations. The stained samples were analyzed under a fluorescent
microscope (Olympus BX60) with dual band (FITC-Texas red) filter and the viability was
calculated as the average of the ratios of live over total cells in a given field.
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Figure 4.11 LIVE/DEAD® assay of chondrocytes. (a) Trypan Blue exclusion assay and (b)
calcein AM and ethidium homodimer-1 LIVE/DEAD® assay immediately after 3D printing.
Scale bars are 50 μm.
Tissue level viability of the bionic ear was assessed using fluorescent staining at various
sites in the neocartilage tissue of the ear. Specifically, the chondrocytes were stained with 2
μg/mL fluorescein diacetate (FDA) and 0.1 mg/mL propidium iodide (PI). The viability of the
cartilage tissue that was in contact with the coil antenna was examined at various locations. To
examine the viability of the tissue at the interface of the cartilage tissue and the electrode, a cross
section of the ear was taken and assay was performed on the cells that were in contact with the
electrode.
4.9.6 Biochemical Analyses
Biochemical analysis was performed on the 3D printed ear under various stages of culture to
determine the cell proliferation and ECM characterization. Samples were removed from the ear
under culture, weighed and kept frozen. Samples were then digested in 1 mL of papain digest
133
buffer (0.1 M sodium phosphate, 10 mM sodium EDTA, 10 mM cysteine hydrochloride, and 3.8
U/mL papain, all from Sigma Aldrich, St. Louis, MO) at 65 °C for 24 h.
Chondrocyte proliferation in the bionic ear under culture was determined by measuring
the DNA content of the samples. In short, the DNA content was quantified by measuring the
amount of fluorescence (358/458 nm) after exposing to Hoechst 33258 dye.35
To convert the
obtained fluorescence from the samples to a quantified value in terms of weight, the fluorescence
was compared with a standard curve created with calf thymus DNA (Fig. 4.12).
Figure 4.12 DNA content standard curve obtained from calf thymus DNA.
Hoechst 33258 dye was kept as a stock solution of 1 mg/mL in distilled water and stored
in a foil-wrapped container at 4 °C. A working solution was diluted to 0.1 μg/mL in 10 mM Tris,
1 mM Na EDTA, 0.1 mM NaCl, pH 7.4, immediately before use and was dispensed by minimal
exposure to light. Calf thymus DNA was made to 100 μg/ml in PBS and stored frozen. Next, the
emission and excitation spectra (358/458 nm) were measured for the Hoechst 33258 dye alone
134
and in the presence of calf thymus DNA and papain digested chondrocytes from the samples
(Fig. 4.13).
Figure 4.13 DNA content in the 3D printed ear at various stages during culture with 20% FBS
(red) and 10% FBS (blue). Error bars show standard deviation with N=3.
Analysis of the contents of the extracellular matrix (ECM) was performed to evaluate the
metabolic profile of the 3D printed ear under culture. The amount of collagen content – a major
component of the extracellular matrix secreted by the chondrocytes under culture – was
determined from the measurement of HYP in the digest.36
The amount of HYP in the sample was
determined from the absorbance measured using a standard curve created from L-
Hydroxyproline (Sigma Aldrich) (Fig.4.14). The samples were first hydrolyzed in 6 N HCl at
110 ºC for 18 h in a test tube. The volume of the sample containing an estimate of 0.2-6 μg HYP
135
was brought to 2 mL. The pH of the solution was also adjusted to the pH of chloramine-T
reagent. The 2 mL sample was then mixed in a test tube with 1 mL chloramine-T solution both
having a temperature of about 20 ºC and kept for about 15 minutes. 1 mL of the
aldehyde/perchloric acid solution was then added and mixed thoroughly. The temperature of the
sample was then kept at 60 ºC by immersing in to a hot water bath for about 20 minutes. The test
tube was then cooled to room temperature under running water and absorbance was detected at
560 nm with a spectrophotometer.
Figure 4.14 Hydroxyproline standard curve obtained from L-Hydroxyproline.
The proteoglycan content in the ECM was evaluated by the quantification of the total
sulfated GAGs in the sample. The GAG assay was performed by the spectrophotometric
detection of the chromatic changes that occur when 1,9-dimethylmethyline blue (DMB), a
136
cationic dye, binds to the sulfate and carboxyl groups present in the GAG chain. To eliminate
interference from the binding of DMB with the carboxyl groups in the alginate, the assay was
performed at a pH of 1.5, which has been shown to block the effect from the alginate. Stable
solutions of the DMB dye were prepared according to standard protocols 37
and mixed with the
sample digest, and the absorbance at 595 nm was read. A standard curve was created using
Chondroitin-6-Sulfate (C-6-S) from shark cartilage (Sigma Aldrich) and used to obtain the
quantitative values of the GAG content from the observed absorbance (Fig. 4.15).
.
Figure 4.15 GAG standard curve obtained from Chondroitin-6-Sulphate.
4.9.7 Histologic Evaluation of the Bionic Ear
We performed basic histological analysis for the general assessment of cell and tissue
morphology and distribution using the hematoxylin-eosin stain.38
For the histologic evaluation of
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the cartilage tissue formed in the bionic ear under culture, specimens were removed from the ear
after 6 weeks and 10 weeks of in vitro culture and kept frozen. The specimens were then fixed in
10% unbuffered formalin supplemented to 0.1 M in CaCl2 for about 24 hours and then embedded
in paraffin. The specimens were coarsely sectioned using a razor blade, followed by a
microtome. For hematoxylin-eosin staining, the sections were first rinsed with 3 changes of 5
minutes in xylene followed by rinsing in 95% ethanol for 2 minutes. The sections were then
immersed in Mayer’s hematoxylin solution (1 g potassium ammonium, 1 g Hematoxylin, 0.2 g
sodium iodide and 1 g citric acid in 1000 mL distilled water) for 10 minutes. The sections taken
out of the staining solution were rinsed in running tap water and in 95% ethanol. The sections
were then immersed in 0.25% Eosin Y solution (250 mL of Eosin Y stock solution and 5 mL of
glacial acetic acid in 800 mL of 80% ethanol) for a minute followed by 3 changes in 100%
alcohol. Finally, the sections were mounted on a glass slide and rinsed with xylene.
The sections were also stained with Safranin O to visualize the amount of proteoglycan
content. The sections were deparaffinized and hydrated using distilled water followed by
immersing in Weigert’s Iron Hematoxylin for 5 minutes. The sections were washed gently in
distilled water few times until the excess dye is removed. The tissue was then differentiated in
1% acid- alcohol (100 mL of 70% ethanol and 1 mL of glacial acetic acid) solution for 5 seconds
and rinsed thoroughly in distilled water. The sections were subsequently immersed in 0.02% Fast
green (0.05 g of Fast green in 25 mL distilled water) for approximately 1 minute, followed by
1% acetic acid for 30 seconds. The staining was completed via immersing in 1% Safranin O
(2.5g Safranin O in 250 mL of distilled water) for 10 minutes. The sections were then gently
rinsed in 95% ethanol and slowly dehydrated by 2 changes in 95% ethanol and 2 changes in
100% ethanol. The stained sections were mounted on cover slips and rinsed with xylene.
138
The stained sections were examined with transmitted light microscopy on a Nikon
Eclipse 50i microscope (Nikon, Melville, N.Y.). All images were recorded with a DXM 1200F
Nikon color digital camera.
4.9.8 Biomechanical Characterization
To characterize the tensile properties of the neocartilage tissue in the 3D printed bionic ear,
dogbone samples were 3D printed in the same chondrocytes density (~60 million cells/mL) as
the bionic ear and at a lower density (20 million cells/mL) for comparison, and cultured under
similar conditions for 10 weeks. Samples from various points in the culture were retrieved and
uniaxial tensile testing was performed with an Instron 5848 Microtester (Instron, Canton, MA) 39
(Fig. 4.16). Prior to testing, the dimensions of the sample in the gauge area were measured using
a digital caliper. The samples were then clamped between serrated grips. A pre-load (< 0.5 N)
was applied to ensure proper seating of the sample. The samples were then extended at a strain
rate of 0.1% of their gauge length per second until failure occurred. Stiffness of the samples was
determined from the linear region of the load-elongation curves. Young’s moduli were calculated
using the measured cross sectional area and gauge length.
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Figure 4.16 Tensile testing of 3D printed dog bone samples. (a) 3D model of the dog bone
sample. (b) Image of the 3D printed dog bone sample under culture and (c) out of culture. (d-e)
Tensile testing of the dog bone sample using Instron 5848 microtester. (f) Image of the sample
after failure. (g) Representative load-elongation curves for the dog bone samples. Scale bars are
1 cm.
Hardness of the cartilage tissue after 10 weeks of culturing was determined by
nanoindentation measurements at various anatomic sites of the ear auricle. Samples were tested
on a Hysitron TriboIndenter (Hysitron Inc., Minneapolis, MN) using a 100 μm radius of
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curvature conospherical diamond probe tip40
(Fig. 4.17). The round tip was chosen instead of a
sharp tip to allow for better conformity during the contact to the tissue sample. A standard
trapezoidal loading profile with a loading rate of 20 μN/s, a peak load of 200 μN, and a hold
period of five seconds was applied in three repetitions to ten sites in each sample. The method of
Oliver and Pharr was used to obtain reduced modulus (Er) and hardness (H) from the unloading
curves.41
The reduced modulus is related to Young’s modulus, E, by 1/Er = (1-ν12)/E1 + (1-
ν22)/E2, where subscript 1 refers to the indenter material, subscript 2 refers to the indented
material, and ν is Poisson’s ratio. The ideal spherical tip function was used to calculate the
projected contact area at the maximum load.
Figure 4.17 Hardness measurement of the 3D printed ear cartilage. (a) Image of the
nanoindentation setup using a Hysitron TriboScope. (b) Representative load-displacement curves
for the 3D printed cartilage.
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4.10 Conclusion
Our strategy of fabricating designer “cyborg ears” represents a proof of principle of
combining the versatility of additive manufacturing techniques with novel tissue engineering
concepts. The cellular self-assembly into tissues draws on the principles of developmental
biology to offer three dimensional intertwining of biology and electronics. The result is the
generation of bona fide bionic organs in both form and function, as validated by tissue
engineering benchmarks and electrical measurements, with the latter demonstrating
“superhuman” capabilities. This concept of co-3D printing interlaced biological, structural, and
electronic components thus represents a new, general strategy in merging electronics with
biological systems. Such hybrids are distinct from either engineered tissue or planar/flexible
electronics and offer a unique way of attaining a seamless integration of electronics with tissues
to generate “off-the-shelf” cyborg organs. Finally, future work will explore the incorporation of
other classes of materials, such as piezoelectrics, for acoustic-to-electric signal transduction.
142
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Chapter 5
3D Printed Bionic Leaves for Photosynthetic
Bioelectricity
5.1 Overview
This chapter presents preliminary results on our attempts to use 3D printing to create a bionic
leaf, by assembling isolated thylakoid photosynthetic functional units with graphene nanoribbon
electronics into a leaf-shaped hierarchical structure for harvesting photosynthetic bioelectricity
(Fig. 5.1).
148
Figure 5.1. Schematic illustration of the bionic leaf architecture showing the hierarchical
integration of functional components via the 3D printing process and the generation of
photosynthetic bioelectricity.
5.2 Introduction
Leaf is a plant’s photosynthetic organ, serving as reaction centers for food energy production.
The whole structure of a natural leaf is evolutionarily tailored to efficiently perform the various
photosynthetic tasks such as - efficient light harvesting by the lens like epidermal cells,
photolytic water splitting by high surface area thylakoid cylindrical stacks (granum) in
chloroplast and the transport of water and photosynthates through the network of vascular
bundles, to and from chloroplasts, the organelles that perform photosynthesis within the
mesophyll cells1-3
. The vascular bundle consists of two conducting channels, xylem and phloem,
respectively for conduction of the primary photosynthetic raw material -water-towards the
chloroplasts and the carrying away of the photosynthetic outputs for storage and consumption at
various sites.
Natural leaf is thus a hierarchical arrangement of several functional components into a
highly efficient photosynthetic machinery4. The creation of an efficient bionic system by
integrating functional components that mimic the photosynthetic machinery of natural leaf for
efficient capture of sunlight photons, oxidation of water to generate high energy electrons and its
conduction away from the reaction centers, would be a major development in biomimetic ways
for energy harvesting. Chloroplasts enclose thylakoid membranes which are the centers of light
dependent reaction of photosynthesis, suspended in the chloroplast stroma, where ultimately the
production of food is taken place via Calvin cycle. Specifically, the photosynthetic unit
149
assembled in the thylakoid membrane consists of antenna pigments and reaction centers
involving two photosystems (I & II). The absorption of light causes an electron to be ejected
from the Chlorophyll reaction centers and is then transferred vectorially via a pathway consisting
of various mediators through a series of redox reactions from the inner to the outer section of the
membrane5. The photosynthetic reaction centers present in the thylakoids are able to use the
absorbed light energy to split H2O and generate O2, H+, a pH gradient and high energy electrons
(e-) with a quantum efficiency of nearly 100% (ie.one quantum of light yields to one electron
transfer). The energy from the pH gradient is subsequently used to produce sugars and
polysaccharides in the Calvin cycle of the photosynthesis11
.
The unmatched quantum efficiency boasted by the natural photosynthetic process has
attracted a lot of interests in the recent years for energy conversion applications. There have been
attempts for harvesting the biomass stored as polysaccharide for the production of bioelectricity
by utilizing microbial fuel cell systems. However, the maximum efficiency for converting the
absorbed solar energy in to polysaccharides by a photosynthetic organism is a only 27%6-11
.
Also, conversion of biomass in to a form of energy that can be utilized and stored easily will
involve additional steps which will in turn reduce the overall efficiency. As an alternative, the
extraction of high energy electron from the photosynthetic electron transport chain before they
are used to fix CO2 in the Calvin cycle could lead to light energy conversion with higher
efficiency. Interestingly, the study done with nanoelectrodes inserted into Chlamydomonas
reinhardtii unicellular algal cells demonstrated the feasibility of this concept for direct extraction
of photosynthetic electrons11
.
However, the utilization of whole photosynthetic cells (Mesophyll, cyanobacterial or
algal cells) for this purpose suffers from the drawbacks of having respiration competing with
150
photosynthesis in sharing the electron transfer pathways and also for providing nutrients to
sustain12,13
. In addition for direct light–electricity conversion applications, it is preferable to use a
higher order plant based system that uses only water as the electron donor such as PSII, rather
than isolated PSI complexes, which require an alternate electron donor. However, when isolated
plant photosynthetic systems directly immobilized on electrodes were used, they suffered from
degeneration of the biomolecules and poor electrical communication14,15
. On the other hand,
utilization of thylakoids, the photosynthetic organelles that performs the light dependent reaction
and houses the reaction center complexes, offers the advantages of high individual protein
stability, fairly simpler immobilization procedures and multiple electron transfer routes. Recent
study involving immobilized thylakoid membranes on multi-walled carbon nanotubes proved the
feasibility of the electron transfer from oxygen evolving complex (OEC) sites to the electrode
achieved via various points in the electron transfer pathway, in addition to a direct transfer from
PSII13
. Therefore using thylakoids as photo-biocatalysts should offer the potential for high
photo-electrochemical activity as well as high stability for energy conversion applications16
.
All of the previous attempts in mimicking the photosynthetic energy conversion of the
natural leaves focused only on replicating the functionality but did not pay attention to the
geometrical architecture. However, complete utilization of photosynthetic functionality of the
thylakoid functional components and efficient collection of bioelectricity, demands that the
bionic system that we engineer to both have similar geometrical architecture for the efficient
performance of primary photosynthetic reaction and analogous functional modules, which could
i) transport the primary photosynthetic raw material, water to the thylakoid lumen and ii)
transfer the electron generated via photolysis of water away from the reaction center to minimize
151
the wasteful recombination reactions, while synergistically, incorporating the thylakoid based
natural photosynthetic engines.
5.3 3D Printing of Bionic Leaf
Here we describe a novel approach that involves the construction of a Bionic leaf using 3D
printing techniques by copying the complex architecture of leaves, with synergistically
engineered essential functional modules to realize generation and harvesting of photosynthetic
bioelectricity from the natural thylakoid membranes. Specifically, we propose to assemble
isolated thylakoid photosynthetic functional units with graphene nanoribbon based electronic
interfacing material into a leaf-shaped hierarchical structure consisting of functional modules
analogous to the vascular bundles of natural leaf to realize harvesting of light energy for
photosynthetic current generation and conduction (Fig. 5.2 A).
Figure 5.2. 3D Printed Bionic Leaf for Energy (A) Conceptual design of the Bionic Leaf (B)
(top) Fresh spinach leaves and isolated thylakoids. (bottom) Dry GNRs and mixed with
PEDOT:PSS conductive matrix. (C) 3D printing of the thylakoids and electronic conductive
matrix. (D) Image of the Bionic Leaf showing vascular bundles for water input and electrodes for
current output.
152
Electrical interfacing of the thylakoid membranes with organic polymer conduction
medium with dispersed graphene nanoribbons will allow for the collection of photosynthetic e-
from various points in the electron transport pathways (such as plastoquinone (PQ, acceptor side
of PSII) pool or reduced ferredoxin (Fd, acceptor side of PSI)) and conduct them away through
an external circuit (Fig. 5.2B). This will enable generation of photosynthetic bioelectric current
before being utilized for the production of sugars and polysaccharides in the Calvin cycle.
Further, the incorporation of a 3D printed vasculature network that resembles the vascular
bundles in natural leaves consisting of a “bionic xylem” made of cellulose microchannels will
allow for supplying water to the thylakoid lumen and a “bionic phloem” made of Ag electrode
networks will enable transporting the bioelectrons produced for storage (Fig. 5.2 C and D).
Additionally, by using the entire thylakoid membranes instead of isolated photosystem
complexes in our design, we will be able to make electrical interface at various sites of the
electron transfer pathways using conducting polymer/graphene nanoribbon matrix to possibly
achieve high electron transfer flux for photo-current generation.
5.4 Thylakoid Isolation and Characterization
Our preliminary experiments involving the isolation, characterization and 3D printing of
thylakoids have yielded promising results. Thylakoids were isolated from fresh organic spinach
leaves according to previously reported procedures17
. In brief, the cleaned, deveined spinach
leaves were homogenized in a chilled blender. The homogenate was then filtered through four
layers of cheese cloth
153
Figure 5.3. Isolation of Thylakoids (A) Deveining of spinach leaves (B) Fresh spinach leaves
being homogenized in a cold blender (C) Filtration of the homogenate. (D) Image of the filtered
solution (E) Isolated thylakoids after centrifugation.
and the thylakoid membranes are then subsequently isolated from crude cell debris and other
subcellular components after multiple steps of centrifugation at various speeds. The isolated
thylakoids were characterized via optical and fluorescent microscopy using Nile red dye (Acros
organics) (Fig 5.4).
154
Figure 5.4. (A) Optical microscopic image of the isolated thylakoids. (B) Fluorescent
microscopic images of Nile red labelled thylakoids.
5.4.1 Determination of the Chlorophyll Content in Isolated Thylakoids
The chlorophyll concentration in the isolated thylakoids is then determined by mixing with 80%
acetone and filtering through Whatman # 4 filter paper followed by measuring the absorbance at
663nm and 645nm in a spectrophotometer. The chlorophyll concentration was then calculated
using Beer-Lambert law to be 2.799 mg/mL (Fig.5.5).
155
Figure 5.5. Determination of the Chlorophyll content in the isolated thylakoids (A)
Determination of Chlorophyll contents of various isolation methods (B) UV-Vis spectrum of the
isolated thylakoids.
5.5 Photosynthetic Electron Generation: Hill Reaction
Next, the photosynthetic functionality- light induced electron transport via photolysis of water- at
the isolated thylakoid membranes was verified using Hill reaction by using
dichlorophenolindophenol (DCPIP) as the Hill reagent18
as shown below.
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Figure 5.6. Hill Reaction using DCPIP. (A) and (B) Experimental procedure showing the
exposure of the thylakoids + DCPIP to light before measuring the OD (C) Image of cuvette
containing thylakoids alone (D) image of cuvette containing DCPIP alone (E) image of cuvette
containing thylakoids + DCPIP and (F) image of cuvette containing thylakoids + DCPIP after the
exposure to light.
Illumination of DCPIP mixed with thylakoids was found to be readily reduced rendering
a bright blue solution to a pale color, whereas the control measurement done in the absence of
light was found to have no significant change in color, verifying the creation of photosynthetic
electron by the thylakoids in the presence of light (Fig 5.6). Further, to quantitatively measure
157
the change in color of the Hill reagent upon reduction with the photosynthetic electrons, we
measured the absorbance of light in a spectrophotometer.
Figure 5.7. Change in absorbance of the sample containing thylakoids +DCPIP after the
exposure to light. Measurement of absorbance without the exposure to light is used as a control.
A sample of thylakoids mixed with Hill reagent was exposed to light every 30 seconds
and the OD was measured in between. The experiment was conducted for up to 12 minutes (Fig.
5.7). The reduction of the percentage absorbance of the light clearly indicates the reduction of
the Hill reagent and indirectly verifies the production of photosynthetic electrons by the isolated
thylakoids upon the exposure to light. A sample containing thylakoids mixed with the Hill
reagent, where the OD is measured at the same intervals, however not being exposed to light in
between was used as a control and did not show significant change in the percentage absorbance
158
over time. This verifies that the reduction of the DCPIP occurred as a result of the production
photosynthetic electrons by the thylakoid membranes.
5.6 Electronic Conduction Medium- Formulation and Characterization
Next to enable the conduction of the photosynthetic electron away from the reaction center, an
electronic conduction medium was formulated (Fig.5.8)16
.
Figure 5.8. Schematic illustration of the interfacing of organic conduction medium with
thylakoid membranes to conduct the photosynthetic electrons away.
Graphene nano ribbons (GNRs) has been used as conducting material for a number of
application due to its excellent electronic properties. However, the dry powdery nature of the
GNRs does not allow for easy use in an extrusion based 3D printing process. On the other hand,
organic polymer based conducting inks have been widely used as a printable conduction
medium. But, it suffers from low conductivity when compared to solid state electronic
conductors. We therefore formulated our conduction medium from a dispersion of GNRs in a
solution of poly (3,4-ethylenedioxythiophene)/ poly(styrene sulfonate) (PEDOT/PSS) based
electrically conductive polymer (Fig 5.9).
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Figure 5.9. Formulation of the electronic conduction medium (A) Image of the GNR powder
(B) image of GNR mixed with PEDOT:PSS at concentration of 0.3 wt%. (C) plot of conductivity
Vs. concentration of GNRs in wt% in the PEDOT:PSS/GNR mixture.
The electrical conductivity of the dispersion of GNRs in PEDOT:PSS at various weight
percentages was characterized to find out the optimum composition (Fig.5.9). A formulation of
0.2 weight percentage of GNRs in PEDOT:PSS showed a dramatic change in conductivity and
any further increase in the concentration of GNRs did not change the conductivity significantly19
.
This indicated that the percolation threshold of the GNRs in PEDOT:PSS was reached by a
concentration of ~0.2 weight percentage of GNRs. We therefore decided to use a concentration
of ca 0.3 weight percentage of GNRs dispersed in PEDOT:PSS as a conductive matrix to ensure
maximumm conductivity.
5.6.1 Characterization of Electronic Conduction Medium
Next, the electronic properties of the conduction medium were characterized using X-ray
diffraction (XRD) and Raman spectroscopy20
.
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Figure 5.10. XRD characterization of the electronic conduction medium. (bottom) XRD
spectrum of pure PEDOT:PSS (middle) XRD spectrum of GNRs alone and (top) XRD spectrum
of GNRs in PEDOT:PSS.
Figure 5.10 shows the XRD patterns of pure PEDOT:PSS, pure GNRs and PEDOT:PSS
with dispersed GNRs. There was no sharp peaks in the pure PEDOT:PSS films indicative of its
predominantly amorphous nature. The pure GNRs showed a sharp peak around 2Θ value of
around 25.6o. The GNR/PEDOT:PSS mixture showed the characteristic peaks of both the pure
GNRs and PEDOT:PSS but no other additional bands21
. This implies the absence of any covalent
interaction between the dispersed GNRs and PEDO:PSS conducting ink.
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Figure 5.11. Raman spectroscopy of the electronic conduction medium (bottom) Raman
spectrum of GNRs alone. (middle) Raman spectrum of pure PEDOT:PSS. (top) Raman spectrum
of the conducting ink with GNRs in PEDOT:PSS.
Raman spectra of pure GNRs, pure PEDOT:PSS films and the PEDOT:PSS with
dispersed GNRs is shown in Figure 5.11. The Raman spectra of pure PEDOT:PSS showed peaks
at 1143/1097 cm-1
(C-C in-plane bending), 1256 cm-1
(C-C in-plane symmetric stretching), 1365
cm-1
(C-C stretching deformations), 1421 cm-1
(Cα=Cβ symmetric vibrations) and 1521
cm−1
(Cα=Cβ asymmetric vibrations). The Raman spectrum of GNRs /PEDOT:PSS mixture
showed similar peaks to pure PEDOT:PSS with possibly a widened (shoulder) peak between
1250 and 1300 cm-1
. This indicates a certain physio-chemical interaction between the GNRs and
PEDOT:PSS conducting polymer.
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5.7 Photosynthetic Material
The biomimetic photosynthetic material was then synthesized from the isolated thylakoid
membranes and the PEDOT:PSS/GNR conductive matrix at various mixing ratios (Fig.5.12).
Figure 5.12. Formulation of the photosynthetic material as a mixture of the isolated spinach
thylakoids and the conductive ink containing dispersed GNRs in PEDOT:PSS organic
conducting polymer.
Characterization of the photosynthetic material for uniform dispersion of thylakoid membranes
was performed using fluorescent microscopy, SEM and TEM imaging. Figure 5.13 A. shows the
fluorescent microscopic images of the thylakoid membranes uniformly dispersed in the
conducting matrix. Fig.5.13 B and C shows the SEM the TEM of the photosynthetic material
respectively.
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Figure 5.13. Characterization of the photosynthetic material. (A) Fluorescent image of the
photosynthetic material showing fluorescein labelled thylakoids. (B) SEM of the photosynthetic
material with white arrow indicating the embedded thylakoid membrane. (C) TEM of the
photosynthetic material.
5.8 Electrical Testing of the Photosynthetic Material
Next, the changes in the electrical conductivity of the thylakoid/PEDOT:PSS+GNR
photosynthetic matrix in response to light was measured at various mixing ratios. The
photosynthetic material was deposited on to Au interdigitated microelectrodes of separation
150μm and the change in current with the exposure to light was measured at applied bias
voltages of +/- 20V using a probe station. Figure 5.14 shows the percentage change in current
after the exposure to light of the thylakoid/PEDOT:PSS+GNR matrix with increasing weight
percentage of the conducting matrix. Thylakoids alone without the addition of any conducting
medium was observed to show about 5% increase in current after the exposure to light. Current
in matrix consisting of conducting medium without any thylakoids was found to decrease after
being illuminated by light, possibly due to the light induced degradation of the PEDOT: PSS
matrix. It was found that a minimum concentration of about 10 weight percentages of thylakoids
is required to have a positive change in the current after the exposure to light. A concentration of
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about 40 percentage by weight of thylakoids in PEDOT:PSS was found to show the maximum
change in current up on light illumination.
Figure 5.14. Change in current observed from the mixture of photosynthetic material biased at
constant voltages of +/-20V, as a result of the exposure to light, versus weight percentage of the
GNR/PEDOT conductive ink in the mixture.
5.9 3D Printable Bionic Leaf Architecture
A CAD drawing of the bionic leaf was created by drawing analogy to the hierarchical
structure of a natural leaf, consisting of the essential functional modules including
Thylakoid/PEDOT:PSS+GNR bionic photosynthetic material, nanocellulose based bionic xylem
to transport water to the thylakoid lumen, Ag electrode base bionic phloem to transport the
bioelectrons produced for storage and a silicone based transparent epidermis layer (Fig. 5.15).
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We also performed preliminary 3D printing experiments, to test the ability of the 3D printer to
faithfully create leaf architecture with thylakoid/PEDOT:PSS active photosynthetic matrix.
Figure 5.15. CAD of the bionic leaf architecture (A) CAD of the conceptual design of the
Bionic Leaf (B) the design of bionic leaf broken down in to various hierarchical functional
structures.
5.10 Conclusion
In summary, the creation of a bionic leaf structure using additive manufacturing techniques by
mimicking the complex hierarchical structure of native leaves, for the direct harvesting of
photosynthetic bioelectricity was proposed and preliminary experiments were conducted.
Specifically, the possibility of electrical integration of isolated thylakoid membranes with an
organic polymer conductive matrix with dispersed graphene nanoribbons was investigated for
the generation and collection of photosynthetic electrons from the light induced water splitting
reactions in the thylakoid membranes. This enabled the harvesting of photosynthetic
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bioelectricity before being utilized for the food production in the Calvin cycle of the natural
photosynthesis. Further, the possibility of 3D printing of vasculature network that resembles the
vascular bundles in natural leaves consisting of a “bionic xylem” made of nanocellulose
microchannels to provide water to the thylakoid lumen and a “bionic phloem” made of Ag
electrode networks for transporting the bioelectrons produced for storage were also studied.
Future work will address the possibility of incorporating a cathode layer separated by a nafion
based ion permeable membrane for the creation of a full electrochemical cell for light induced
generation of bioelectricity.
5.11 References
1 Nikolopoulos, D., Liakopoulos, G., Drossopoulos, I. & Karabourniotis, G. The
relationship between anatomy and photosynthetic performance of heterobaric leaves.
Plant Physiology 129, 235-243 (2002).
2 Shimoni, E., Rav-Hon, O., Ohad, I., Brumfeld, V. & Reich, Z. Three-dimensional
organization of higher-plant chloroplast thylakoid membranes revealed by electron
tomography. Plant Cell 17, 2580-2586 (2005).
3 Smith, W. K., Vogelmann, T. C., DeLucia, E. H., Bell, D. T. & Shepherd, K. A. Leaf
form and photosynthesis: Do leaf structure and orientation interact to regulate internal
light and carbon dioxide? BioScience 47, 785-793 (1997).
4 Zhou, H. et al. Artificial inorganic leafs for efficient photochemical hydrogen production
inspired by natural photosynthesis. Advanced Materials 22, 951-956 (2010).
5 Szabó, I., Bergantino, E. & Giacometti, G. M. Light and oxygenic photosynthesis:
Energy dissipation as a protection mechanism against photo-oxidation. EMBO Reports 6,
629-634 (2005).
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6 Chaudhuri, S. K. & Lovley, D. R. Electricity generation by direct oxidation of glucose in
mediatorless microbial fuel cells. Nature Biotechnology 21, 1229-1232 (2003).
7 Heyndrickx, M., De Vos, P. & De Ley, J. H2 production from chemostat fermentation of
glucose by Clostridium butyricum and Clostridium pasteurianum in ammonium- and
phosphate limitation. Biotechnology Letters 12, 731-736 (1990).
8 Min, B., Cheng, S. & Logan, B. E. Electricity generation using membrane and salt bridge
microbial fuel cells. Water Research 39, 1675-1686 (2005).
9 Park, D. H. & Zeikus, J. G. Electricity generation in microbial fuel cells using neutral red
as an electronophore. Applied and Environmental Microbiology 66, 1292-1297 (2000).
10 Rosenbaum, M., Schröder, U. & Scholz, F. Utilizing the green alga Chlamydomonas
reinhardtii for microbial electricity generation: A living solar cell. Applied Microbiology
and Biotechnology 68, 753-756 (2005).
11 Ryu, W. et al. Direct extraction of photosynthetic electrons from single algal cells by
nanoprobing system. Nano Letters 10, 1137-1143 (2010).
12 Scherer, S. Do photosynthetic and respiratory electron transport chains share redox
proteins? Trends in Biochemical Sciences 15, 458-462 (1990).
13 Calkins, J. O., Umasankar, Y., O'Neill, H. & Ramasamy, R. P. High photo-
electrochemical activity of thylakoid-carbon nanotube composites for photosynthetic
energy conversion. Energy and Environmental Science 6, 1891-1900 (2013).
14 Mershin, A. et al. Self-assembled photosystem-I biophotovoltaics on nanostructured TiO
2 and ZnO. Scientific Reports 2 (2012).
15 Esper, B., Badura, A. & Rögner, M. Photosynthesis as a power supply for (bio-)hydrogen
production. Trends in Plant Science 11, 543-549 (2006).
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16 Bedford, N. M., Winget, G. D., Srikoundinya, P. & Steckl, A. J. Immobilization of stable
thylakoid vesicles in conductive nanofibers by electrospinning. Biomacromolecules 12,
778-784 (2011).
17 Izawa, S. & Good, N. E. Effect of salts and electron transport on the conformation of
isolated chloroplasts. I. Light-scattering and volume changes. Plant Physiol. 41, 533-543
(1966).
18 Hill, R. Oxygen evolved by isolated chloroplasts [5]. Nature 139, 881-882 (1937).
19 Angelo, P. D., Cole, G. B., Sodhi, R. N. & Farnood, R. R. Conductivity of inkjet-printed
PEDOT:PSS-SWCNTs on uncoated papers. Nordic Pulp and Paper Research Journal
27, 486-495 (2012).
20 Zhou, J. & Lubineau, G. Improving electrical conductivity in polycarbonate
nanocomposites using highly conductive PEDOT/PSS coated MWCNTs. ACS Applied
Materials and Interfaces 5, 6189-6200 (2013).
21 Li, J., Liu, J. C. & Gao, C. J. On the mechanism of conductivity enhancement in
PEDOT/PSS film doped with multi-walled carbon nanotubes. Journal of Polymer
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Chapter 6
Conclusions and Future Outlook
6.1 Summary of Main Conclusions
This thesis presented our explorations for the creation of multidimesionally integrated bionic
systems via the general approach of nanomaterials engineering paired with additive
manufacturing techniques, for applications in energy and biomedical sciences. Specifically, we
presented design development and study, of bionic nanosensors for biointegrated ubiquitous
sensing of pathogenic contaminants, bionic organs with enhanced functionalities by using the
example of a bionic ear with three dimensionally integrated electronics and lastly bionic leaves
for generation and harvesting of photosynthetic bioelectricity.
Chapter 1 introduced the general concept of bionic systems, addressed the design
challenges and discussed general strategies to overcome these challenges. First, a closer look on
the biological components and their features are presented, especially paying attention to their
dichotomies with the functional engineered systems and materials. Next, nanomaterials
engineering as a general strategy to overcome the disparities is introduced, featuring the general
properties and functionalities of most commonly used electronic and structural engineering
nanomaterials. Finally, a library of bio-orthogonal processes and methods are introduced, that
enable a synergistic integration between the fundamental biological functional modules and
nanoscale electronic and structural building blocks.
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Chapter 2 presented our work on the design, development and testing of bionic
nanosensors. Specifically, direct integration of graphene based highly sensitive bionic
nanosensors with biological materials such as tooth enamel, skin, muscle tissue, and food
materials for in situ first order monitoring and detection of pathogenic bacteria is presented. The
key functionalities of the graphene/silk hybrid sensing elements are derived from a synergistic
integration of the individual materials properties and components. Bioselective detection
pathogenic bacteria including H. pylori and S. aureus were demonstrated at clinically relevant
concentrations via self-assembly of antimicrobial peptides onto graphene. Further, the
incorporation of a resonant coil eliminated the need for onboard power and external connections.
Chapter 3 presented the detailed work on the study on antimicrobial peptides (AMP) as a
biomolecular probe on electronic biosensing platforms for the detection of pathogenic bacterial
contaminants. Specifically, peptide sequence corresponding to Magainin II, an antimicrobial
peptide isolated from the skin of African clawed frog, Xenopus Laevis, were immobilized on to
the gold electrodes of an interdigitated capacitive sensor via a C-terminal Cysteine residue. The
AMP functionalized sensors were able to demonstrate semi-selective detection of pathogenic
bacteria including E. coli O157:H7 and S. typhimurium against gram positive bacteria (L.
monocytogens) and non-pathogenic strains of E. coli via impedance spectroscopic measurements.
Further, real-time detection of bacteria was demonstrated using AMP functionalized sensors in a
flow through microchannel for applications such as water quality monitoring.
Chapter 4 presented the work on the creation of a bionic ear with three dimensionally
entwined electronics and cochlear like electrodes using nanomaterials engineering and additive
manufacturing assisted bio-fabrication technique. Specifically, we generated a bionic ear via 3D
printing of a cell-seeded hydrogel matrix in the anatomic geometry of a human ear, along with an
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intertwined conducting polymer consisting of infused silver nanoparticles. This allowed for in
vitro culturing of cartilage tissue around an inductive coil antenna in the ear, which subsequently
enables readout of inductively-coupled signals from cochlea-shaped electrodes. The result is the
generation of bona fide bionic organs in both form and function, as validated by tissue
engineering benchmarks and electrical measurements. The printed ear exhibits enhanced
auditory sensing for radio frequency reception. Overall, this approach suggests means to
intricately merge biological and nanoelectronic functionalities via 3D printing based additive
manufacturing.
Lastly, chapter 5 presented the design, development and characterization of a bionic leaf
enabled by assembling isolated thylakoid photosynthetic functional units with graphene
nanoribbon electronics into a leaf-shaped hierarchical structure for harvesting photosynthetic
bioelectricity. The approach involved the construction of a bionic leaf using 3D printing, by
replicating the complex architecture of leaves, and incorporating engineered essential functional
modules to realize generation and direct harvesting of photosynthetic bioelectricity from
thylakoid membranes. Specifically, we assembled isolated thylakoid photosynthetic functional
units from spinach leaves with interlaced graphene nanoribbons into a leaf-shaped hierarchical
structure containing vascular networks for water flow, to realize harvesting of light energy for
photosynthetic e- generation and conduction. Electrical interfacing of the thylakoid membranes
with organic polymers containing dispersed graphene nanoribbons enables the harvesting of
photosynthetic bioelectricity before being utilized for the food production in the Calvin cycle of
the natural photosynthesis. Ongoing work explores the incorporation of 3D printed vasculature
network that resembles the vascular bundles in natural leaves consisting of a “bionic xylem”
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made of cellulose microchannels to provide water to thylakoid lumen and a “bionic phloem”
made of Ag electrode networks for transporting the bioelectrons produced for storage.
6.2 Outlook
Overall, this thesis has presented considerable advances in the design and development of bionic
systems for applications in biomedical and energy related areas. The approach that we developed
via the pairing of various bio-orthogonal processes that fall under the broader umbrella of
bionanotechnology with additive manufacturing techniques can serve as a general strategy to
overcome the dichotomies between biological systems and functional engineered components,
allowing for a seamless merging and integration between the two.
With regards to graphene based wireless “tooth tattoo sensor”, our results only represent
a prototype, ‘first generation’ platform for biointerfaced graphene nanosensors. Owing to the
semiselective nature of the interaction of AMPs with pathogenic bacteria, differentiation of
multiple species of pathogenic bacteria has not been achieved. Future work could explore the
strategies to improve this selectivity via investigations into multi-ligand and aptamer-based cap-
ture agents, and antibody-based biorecognition molecules with improved stability to provide
stringent discrimination between species of pathogenic bacteria. Exploring alternative strategies
for covalent and non-covalent functionalization of graphene sensors will be also interesting.
Finally, future challenges in the sensor development will involve further miniaturization of the
wireless coil for integration onto a smaller footprint (such as a human tooth) and testing of the
platform on in vivo systems, including tissue and teeth in living animals and humans. Overall
such approaches for the direct interfacing of biosensors onto the human body could enable
applications such as on-body health quality monitoring and adaptive threat detection.
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With regards to the development of bionic organs, our work on bionic ear opens up new
avenues for the development of similar autonomous chimeric bionic systems with advanced
capabilities than their native counter parts. Such method produces biological, electronic and
structural components of a Bionic Organ in a single process in the precise spatial heterogeneity
for each material as prescribed by the CAD design in to the complex anatomic geometry of the
final system. Since electronic circuitry is at the core of sensory and information processing
devices, fully interweaving functional electronic components with biological tissue via 3D
printing enables the growth of “cyborg organs” exhibiting enhanced functionalities over human
physiology. Future work could explore the incorporation of other novel nanoscale functional
building blocks such as graphene nanoribbons (GNR), quantum dots (QD), ferroelectrics,
peizoelectrics and magnetostrictive materials to expand the opportunities to enable versatile
bottom-up assembly of macroscale components possessing tunable functionalities.
With regards to the creation of bionic leaves, our work opens up new opportunities for
the development of bioinspired and biomimetic materials and systems for energy generation and
harvesting. Future work could include the incorporation of a cathode layer, separated by an ion
permeable membrane material such as nafion to the current bionic leaf architecture to create a
complete electro-voltaic cell for photosynthetic current generation without the application of an
external EMF ( Electro motive force). The scaling of the process to create multiple leaves
stacked up in to a tree like architecture would be interesting. Further, through such approaches,
we anticipate to develop fundamental understanding on the possibilities of direct integration of
functional nanomaterials with the natural leaves and plants to explore the opportunities of direct
energy harvesting from green plants.
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Another on-going work in this direction involves the interfacing of nanoengineered
functional devices with biological microorganisms such as motile bacteria to create
multifunctional self-propelling bacterial-nanobionics§. Nano-scale science and engineering in
general, enables the creation of functional devices and structures with precise geometry by
controlling matter at the atomic scales. Such nano-structured objects can be engineered to
possess a wide variety of functionalities such as mechanical, electronic, plasmonic, magnetic,
optical and sensing by exploiting novel properties and phenomena exhibited at these size scales.
However, much of the potential of such nano-objects made possible by the miniaturization
techniques is limited by the challenges in enabling propulsion or actuation to them.
Nanoscale engineering and biological systems are two fields that can mutually benefit
from each other; with nanoscale engineering providing tools to control and modify biological
processes, while biology provides the systems and materials to enable higher functionalities for
nano-engineered tools. A synergistic integration of biological components with abiotic systems
enables ways to design and create hybrid devices with some of the amazing capabilities exhibited
by living systems. For instance, living system composing of biological components possesses the
astounding ability to produce mechanical motion from chemical energy making them an
attractive means to provide actuation and motility to functional abiotic components. For
example, micro-organisms such as bacteria possess a unique ability to move at small length
scales with very high efficiency. In addition bacteria are ubiquitous, which makes their
machinery easily accessible in almost all kinds of environments. Therefore, a direct interfacing
of engineered functional nano objects with motile bacterial cells enables the creation of multi-
functional ‘nanostructure-bacteria hybrid devices’. Significantly, such bacteria-nanostructure
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hybrid devices will be self-propelling in addition to exhibiting the engineered functionality of the
interfaced nanostructures.
In addition to the above mentioned potentially revolutionary technological applications,
our work and oncoming future developments in this direction will broaden our fundamental
understanding of the mechanisms employed in the signal transduction across the biology-
technology interface, i.e., at the interface of biological systems with the novel multi-functional
abiotic materials. For attaining a seamless three dimensional merging of biological systems with
electronic or mechanical components, an efficient transduction of biological events into readily
measurable outputs and the transduction of electronic or optical signals into biologically relevant
actions are required. This demands synthesis and characterization of novel materials with
engineered functionalities to allow for an efficient communication between the biotic/abiotic
interfaces.
In summary, the advances in the seamless integration of functional electronics and
mechanical elements with viable biological systems described in this thesis are indicative of the
immense potential of this technology. Regardless of the directions future work may take, the
results presented in this thesis provide a strong motivation for continued and expanded efforts in
the design and development of bionic systems along this line.
___________________________________
§ The work reported in this section is based on the following manuscript in preparation: T. James et al, Remote
Control of Bacteria using Plasmonic Nanoantenna (manuscript in preparation)+.