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Materials Science and Engineering R 59 (2008) 38–71
Advanced biomaterials for skeletal tissue regeneration: Instructive
and smart functions
F. Barrere a,*, T.A. Mahmood b, K. de Groot a, C.A. van Blitterswijk a
a University of Twente, Department of Tissue Regeneration, 7500 AE Enschede, The Netherlandsb Amgen Inc., Division of Translational Sciences, One Amgen Center Drive, Thousand Oaks, CA 91320, United States
Available online 1 February 2008
Abstract
The past half century has seen explosive growth in the use of medical implants. Orthopedic, cardiac, oral, maxillofacial and plastic surgeons are
examples of medical specialists treating millions of patients each year by implanting devices varying from pace makers, artificial hip joints, breast
and dental implants, to implantable hearing aids. All such medical implants make use of special materials, known as biomaterials, defined as
‘‘materials intended to interface with biological systems to evaluate, treat, augment or replace any tissue, organ, or function of the body’’ [D.F.
Williams, The Williams Dictionnary of Biomaterials, Liverpool University Press, Liverpool, 1999]. While the priority for the first generation of
biomaterials was inertness with living tissues, the field is shifting towards biologically active systems in order to improve their performance and to
expand their use. Biomaterials can be combined as scaffolds with cells (i.e. tissue engineering), growth factors or genetic material in order to trigger
tissue regeneration. In addition, recent reports have shown the possibility to design biomaterials that can activate cellular processes and tissue
formation solely by their intrinsic physicochemical and three dimensional spatial properties. This article reviews the recent developments in the
design of biomaterials that integrate our understanding of cellular and molecular mechanisms with materials science. After an overview of the
physicochemical and biological processes occurring at the interface between the biomaterials and biological milieu, we will address the biological
principles contributing to the design and engineering of advanced biomaterials for application towards recent therapeutic strategies for tissue
regeneration. Finally, future directions for the design of advanced biomaterials will be discussed.
# 2007 Elsevier B.V. All rights reserved.
Keywords: Skeletal tissue; Medical implant; Biomaterials; Tissue Engineering
Contents
1. Introduction . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 39
2. Hard skeletal tissues. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 40
2.1. Structural and compositional organization . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 40
2.1.1. Physical and chemical component . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 40
2.1.2. Cellular components . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 41
2.1.3. Biological properties. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 42
2.2. Self repair of hard tissues: example of smart materials . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 43
3. Soft skeletal tissues . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 43
3.1. Structural and compositional organization of cartilage . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 43
3.1.1. Physical and chemical components . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 43
3.1.2. Cellular component. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44
3.1.3. Biological properties. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44
3.1.4. Intrinsic cartilage tissue repair . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44
4. Current strategies to repair skeletal tissues . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44
4.1. Biomaterials . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44
4.2. Cell-based therapies . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 45
* Corresponding author. Current address: Kuros Biosurgery AG, Technoparkstrasse 1, 8005 Zurich, Switzerland. Tel.: +41 44 200 56 52; fax: +41 44 200 57 52.
E-mail address: [email protected] (F. Barrere).
0927-796X/$ – see front matter # 2007 Elsevier B.V. All rights reserved.
doi:10.1016/j.mser.2007.12.001
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 39
4.3. Towards smart designs to repair tissues . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 47
4.3.1. Biomimetic materials for skeletal repair . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 47
4.3.2. Tissue engineering . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 48
4.3.3. Materials for tissue engineering . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 48
5. Instructing physico-chemical and biological processes at biomaterial interfaces. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 52
5.1. Osteoinductive biomaterials . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 52
5.2. Orchestrating biomaterials degradation with new tissue formation . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 54
5.2.1. Degradation mechanisms . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 54
5.2.2. Smart degradation designs . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 54
5.3. The role of proteins in regulating biomaterial-induced biological response . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 55
5.3.1. Protein adsorption onto biomaterials . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 56
5.3.2. Smart designs to control protein adsorption . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 56
5.4. Controlling cell–biomaterial interactions . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 57
5.4.1. Cellular activities and functions on biomaterials. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 57
5.4.2. Effect of surface physico-chemistry . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 59
5.4.3. Effect of topography . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 59
5.4.4. Micro- and nanodesigns of biomaterials . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 60
5.5. Multi-functional scaffolds . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 60
5.5.1. Multiple-component scaffolds . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 61
5.5.2. Multidrug delivery . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 61
5.6. Three-dimensional control of biomaterials on cells and tissues. . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 62
5.7. Physical stimuli on cells . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 63
6. Concluding remarks . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 64
Acknowledgements . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 65
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 65
1. Introduction
The past half century has seen explosive growth in the use of
medical implants. Orthopedic, cardiac, oral, maxillofacial and
plastic surgeons are only examples of medical specialists
treating millions of patients each year by implanting devices as
diverse as pace makers, artificial hip joints, breast implants, to
dental implants and implantable hearing aids. The cost of
treating diseases and problems caused by loss of tissue
function, now exceeds US$39 billion in North America alone
[2]. In addition, an aging population and increasing life
expectancy in the developed world now means that our tissues
and organs are pressed into service longer than they may be able
to independently withstand.
So what has been done to deal with these modalities? To
date, in cases where pharmacological treatments alone have
been insufficient, the principal approach has been the
transplantation of organs and tissues from other people
(allogeneic transplantation) or moving tissue from healthy
parts of the patient to diseased areas (autologous transplanta-
tion) [3,4]. The scarcity of donors compounded with issues of
transplant rejection and donor site morbidity stimulated early
research into replacing sophisticated tissues and organs with
artificial, man-made substitutes. To date, tens of millions of
individuals have had the quality of their lives enhanced for as
long as 25 years by the use of these man-made implants [5].
However, far from being long-term replacements, early devices
such as the Jarvik heart became temporary devices for
critically-ill patients waiting for heart transplants. The question
of how to solve the tissue and organ transplant problem
remained unanswered.
The lack of efficacy seen by using biomaterials alone has
been due to their poor responsiveness in comparison with the
flexibility and reactivity of natural tissues and organs. Materials
scientists alone cannot solve this complex biological issue as
these biomaterials by definition must interact with, and function
in living entities. Nowadays, the strategy to design smart
biomaterials lies in their capacity to instruct biological entities
to entirely regenerate tissues; in other words, to create a
synthetic twin tissue or organ that can function as its natural,
original tissue.
This strategy started in the late 1960s by Larry Hench.
Horrified by the amputation of limbs of thousands of Vietnam
War battlefied casualties, he started to design biomaterials ‘‘to
repair people, instead of making materials to destroy them’’
[5,6]. To do so, he hypothesized that an implant containing
calcium and phosphate in proportions similar to bone mineral
would not be rejected by the body. Indeed, a physicochemical
bond was observed between the biomaterials designed by
Hench (Bioglass1) and the hosting bone. To date, although
calcium phosphate biomaterials are relatively ‘‘old’’, their
ability to trigger bone formation is incomparable with other
biomaterials. However, these bone mineral-like substitutes
cannot substitute the bones’ mechanical function, illustrating
the as yet unmet medical need that is the driver behind our
ultimate goal of developing a synthetic entity that would
entirely substitute and regenerate a damaged tissue or organ.
Today, the way to deal with this issue remains similar to
Hench’s strategy. We aim at creating synthetics with the
appropriate and full responsiveness towards biological milieu,
i.e. smart systems. To do so, we continuously investigate
biological mechanisms occurring in tissues and organs, and at
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7140
biomaterial interfaces at the molecular, cellular and macro-
scopic levels in, order to pinpoint the critical phenomena that
can help us understand the fundamental processes that occur in
these systems. Knowledge of these mechanism is crucial to
create, a man-made substitute that could heal over the long-
term. Naturally, the biomaterials’ field is shifting towards
biologically active systems in order to improve their
performance and to expand their use. Biomaterials have
combined them as scaffold with autologous cells (i.e. tissue
engineering), to render tissue substitutes more ‘‘alive’’ and
more reactive towards biological environment. More recently,
there has been considerable interest in the development of
‘‘smart materials’’ that are able to instruct the behavior of
adhered or encapsulated cells by releasing bioactive molecules
into the local environment, or through extracellular protein/
peptide mimetics built into the delivery substrates [7,8].
However, the ability of materials to modulate downstream gene
response without exogenous growth factors, coatings or
complex ligand incorporation has the potential to greatly
facilitate the development of tissue engineering and cellular
therapies. As an illustration of this concept, a class of biphasic
calcium phosphate ceramic induced de novo bone formation at
non-osseous sites in vivo without requiring the delivery of cells
or biologic compounds [9], suggesting that the surface
chemistry of the ceramic allowed the selective adsorption of
morphogenetic proteins that trigger osteogenesis. It was also
demonstrated using polymer libraries that substrate chemistry
can influence the developmental lineages of embryonic stem
cells [7]. Although the use of embryonic stem cells lineages is
far from clinical applications in skeletal repair and will not be
discussed in this review, this pioneer study illustrates the
potential of biomaterials in directing cellular differentiation.
This article reviews recent developments and approaches in
the design of smart biomaterials that integrate cellular and
molecular biology in order instruct the biological milieu with
the ultimate goal of total tissue regeneration.
2. Hard skeletal tissues
Some 540 million years ago, within a period of a few million
years, a multitude of primarily multicellular organisms began to
produce mineralized structures that are widespread among the
mollusks, the vertebrates, echinoderms, plants and protoctists.
These mineralized structures were formed in order to fulfill
either specific or multipurpose functions [10]. In vertebrates,
besides the presence (negligible in weight) of tiny magnetite
minerals in human brains that are responsible for orientation,
navigation and homing skills [11], apatitic calcium phosphate
apatite is the main body’s mineral component. It is present in
hard tissues, i.e. bone and teeth, whose functions are structural
protection, motion and mastication. Bone is the component of
the skeletal system, which is involved in the protection, support
and motion of the body. Flexible and elastic, bones from the rib
cages protect heart, lungs and other organs which function
involves motion, expansion and contraction. Being stiff, bone
structurally supports the mechanical action of soft tissues, like
the contraction of muscles or expansion of lung. At a cellular
level, bone is a protective and production site for specialized
tissues such as bone marrow, which is a blood-forming system.
Finally, it is a mineral reservoir used by endocrine systems to
regulate the calcium and phosphate homeostasis in the
circulating body fluids.
Hard tissues are smart, labile and reactive towards their
environment. Their formation, their structure and adaptations
are induced by a highly complex physico-chemical and cellular
machinery.
2.1. Structural and compositional organization
2.1.1. Physical and chemical component
In shape and macrostructure, bones and teeth are affected by
genetic, metabolic and mechanical factors and functions. For
example, broad, flat plates, such as scapulae, anchor large
muscle masses, whereas hollow and thick-walled tubes, such as
the femur or radius, support weight. All bone consists of a basic
dual structure, for which their importance varies with the
function. An external layer, or cortex, covers the bone; it is
smooth, continuous and dense (approximately 1.80 g/cm3). In
the interior, cancellous bone is porous with an average porosity
of 75–95% and an average density of 0.2 g/cm3. However, bone
characteristics vary with age and site.
The mechanical properties of bone reconcile high stiffness
and high elasticity in a manner that is not yet possible with
synthetic materials. Cortical bone specimens have been found
to have tensile strength in the range of 78.8–151.0 MPa in
longitudinal direction and 51.0–56.0 MPa in transversal
direction. Bone’s elasticity is also important for its function
giving the ability to the skeleton to withstand impact. Estimates
of modulus of elasticity of bone samples are of the order of
17.0–20.0 GPa in longitudinal direction and of 6.0–13.0 GPa in
the transversal direction [12]. These remarkable mechanical
properties are due to the microstructure of bone combining an
organic matrix with mineral (calcium phosphate apatite)
crystals which are usually oriented in the longitudinal direction
of bone giving higher strength and stiffness in the longitudinal
axis than transversally.
By weight, bone mineral and dentin (inner part of the tooth)
contains approximately 60% mineral, 10% water and about
30% organic matrix (90% type I collagen and 10%
proteoglycans and numerous non collagenous proteins), while
mature enamel is composed of more than 90% mineral and less
than 10% organic matrix (mainly amelogenin). The structure of
human apatitic calcium phosphate biominerals (bone, dentin,
enamel) can be represented as:
Ca10�ðx�uÞðPO4Þ6�xðHPO4 or CO3ÞxðOH; F . . .Þ2�ðx�2uÞ
with 0 � x � 2 and 0 � 2u � x
in which (x � u) cationic vacancies and (x � 2u) monovalent
anionic vacancies coexist.
The u parameter appears generally very small and it can be
neglected. Two types of carbonate ions are present located on
the trivalent and monovalent anionic sites of the structure [13].
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 41
For bone and dentin, the proportion of cationic vacancies is
very high and close to the maximum, whereas it is very low for
dental enamel.
Bone and dentin apatites start to nucleate into the nanopores
present in the collagen fibrils [14] as the extracellular fluids are
supersaturated in calcium and phosphates ions. This hetero-
geneous nucleation is catalyzed by the presence of phosphated
esters groups [15] and carboxylate groups [16] at the surface of
collagen fibrils. Along these fibrils, crystallization takes place
to finally interconnect the entire collagen network. These
apatitic crystals are formed of thin plates of irregular shapes.
Their sizes range in length from 20 A for the smallest particles,
to 1100 A for the largest particles [17,18]. This results in a very
large surface area facing extracellular fluids. This property is
critically important for the rapid exchange of ions with these
fluids. The crystallization process of enamel is different than for
bone or dentin: amelogenin being hydrophobic self-assembles
into nanospheres that guide the growth of the ribbon-like dental
enamel crystals. Indeed, enamel crystals are tens of microns
long with an aspect ratio (length/width) of at least 1000 [19].
These physico-chemical differences between these human
apatites are related to their biological function. The collagen–
nanocrystals composite structure of bone meets the mechanical
requirements of the body. In addition, the high specific surface
area [20] and the numerous crystallographic vacancies of bone
crystals, are responsible of numerous ionic exchanges. In fact
bone acts as a calcium and phosphate reservoir for the entire
body. Enamel mineral content is higher than the one of bone,
and its crystalline structure is also more cohesive and stable in
order to resist to acid etching and abrasion often occurring
during mastication. The shape of enamel crystals is also
optimized for a maximal kinetic of growth that may facilitate
remineralization from saliva [13].
2.1.2. Cellular components
Skeletal tissues originate mostly from mesenchymal stem
cells during embryonic development. In the adult stage,
mesenchymal stem cells can be isolated from bone marrow,
adipose tissues, amniotic membrane or umbilical cord
perivascular tissue [21,22]. Mesenchymal stem cells are, by
definition, of self-renewal capacity to repopulate all the
Table 1
Bone cells and their associated functions and markers
Name Function
Osteorpogenitor High proliferative potential
Differentiation in bone lineage
Osteoblast Non proliferative cells
Highly differentiated
Bone mineralization
Osteoclast Bone resorption
Signaling osteoblasts to form new bone
appropriate cell lineages. They are multipotent cells that can
differentiate into osteoblastic, myoblastic, adipogenic, chon-
drogenic, endothelial and neurogenic lineage through a multi-
step differentiation sequence as follows: proliferation, commit-
ment, lineage progression, differentiation and maturation.
Regarding bone tissue, its formation takes place in an organism
during (i) embryonic development, (ii) growth, (iii) remodel-
ing, (iv) fracture healing, and (iv) after ectopic implantation of
osteoinductive matrices. The cells that are involved in
osteogenesis throughout life are summarized in Table 1 [23].
2.1.2.1. Osteoprogenitor cells. With regard to the osteogenic
lineage, mesenchymal stem cells sustain a cascade of
differentiation steps as described by the following sequence:
Mesenchymal stem cell! immature osteoprogenitor! ma-
mature osteoprogenitor! pre-osteoblast! mature osteo-
blast! osteocyte or lining cell. The later the differentiation
stage, the lower the capacity for self renewal and cell
proliferation [23]. In bone marrow, which to date has been
the most common source for harvesting mesenchymal stem
cells, osteoprogenitor cells represent a very small percentage
(less than 0.005%) of nucleated cell types in healthy adult bone
[24]. Differentiating osteoprogenitor cells express several bone
matrix macromolecules, namely alkaline phosphatase, collagen
type I, bone sialoprotein, osteocalcin, osteopontin [25].
2.1.2.2. Osteoblasts. Mature osteoblasts are non-migratory
and highly differentiated cells that can differ substantially in
their properties depending on their stage of development, from
which their function and phenotype can vary and be divided
into four categories: (i) active osteoblasts are cuboidal in shape,
mononuclear and rich in alkaline phosphatase activity. They
synthesize and secrete collagen type I and glycoproteins
(osteopontin, osteocalcin), cytokines and growth factors into a
region of unmineralized matrix (osteoid) between the cell body
and the mineralized matrix [26]. Osteoblasts also produce
calcium phosphate minerals extra- and intracellularly within
vesicles [27]. (ii) osteocytes are mature osteoblasts which have
become trapped within the bone matrix and are responsible for
bone maintenance and homeostasis. (iii) Bone lining cells are
found along the bone surfaces that undergo neither de novo
Markers Origin
Alkaline phosphatase activity Mesenchymal
Type 1 collagen
Bone sialopontin
Osteocalcin
Osteopontin
Alkaline phosphatase activity Mesenchymal
Calcium phosphate
Bone sialopontin
Osteocalcin
Osteopontin
Tartrate resistent acid phosphatase Hematopoietic
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7142
bone formation nor resorption. (iv) Inactive osteoblasts are
elongated cells, undistinguishable morphologically form the
bone lining cells. Only active osteoblasts and their precursors
contribute to bone formation (Fig. 1).
2.1.2.3. Osteoclasts. Osteoclasts are derived from hemato-
poietic stem cells that differentiate along the monocyte/
macrophage lineage. They are responsible for bone resorption
by acidification of bone mineral leading to its dissolution, and
by enzymatic degradation of demineralized extracellular bone
matrix. The mature osteoclast is a functionally polarized cell
that attaches via its apical pole to the mineralized bone matrix
by forming a tight ring-like zone of adhesion, known as the
sealing zone. In the resorbing compartment, situated under the
cell and delimited by the sealing zone, osteoclasts generate an
acidic milieu that results in the dissolution of bone mineral.
This osteoclastic acidification is mediated by the action of
carbonic anhydrase that produces carbon dioxide, water and
protons that are extruded across the cell membrane into the
resorbing compartment [26]. During bone remodeling, osteo-
clasts resorb old bone, and via local paracrine signaling
molecules, activate osteoblasts to form new bone.
2.1.3. Biological properties
Bone is a highly vascular, living and dynamic tissue, which
is remarkable for its hardness and regenerative capacity. In its
mineralized matrix, bone embeds osteocytes that constitute the
major cell type in mature bone. Vascular canals ramify within
Fig. 1. Diagram representing the structure of bone (a) and cartilage (b) and their a
apatitic nanocrystals. Osteoblasts derive from mesenchymal stem cells. They are resp
osteocytes. Osteoclasts are responsible for bone resorption, they initiate the mechanis
distribution at the various depths of tissue are shown. A: articulating surface, S:
subchondral bone, CB: cancellous bone (diagram adapted from Woodfield et al. [4
bone, providing its cells with metabolic support. The outer and
inner surfaces of bone are lined by periosteum and endosteum, a
fibrocellular layer, where osteoblasts and osteoclasts are
respectively located. In cancellous bone, the pores are filled
with blood vessels, as well as red and yellow marrow. Red bone
marrow includes cells which participate in the maintenance and
organization of bone, namely osteoprogenitor cells osteoblasts
and osteoclasts. The yellow bone marrow is composed of fat
cells.
In contrast with dental tissue, bone is a very dynamic tissue.
After the initial ossification of the embryonic skeleton,
osteoclasts and osteoblasts begin the modeling and remodeling
processes. In general, modeling refers to alteration in the shape;
whereas remodeling refers to turnover of bone that does not
alter the shape; however, the two processes often occur
simultaneously and the distinctions between them may not be
readily apparent. During skeletal growth, removal and
replacement of bone proceeds at a rapid pace. The rate of
turnover of the skeleton approaches 100% per year in the first
year of life, declining to about 10% per year in late childhood,
and then usually continues at approximately this rate or more
slowly throughout life. Much of the turnover of bone during
growth results from bone-modeling, but presumably at least
some remodeling also occurs. After the completion of skeletal
growth, the turnover of bone results primarily from remodeling.
Modeling and remodeling result from coordinated resorption
and formation of bone over extensive regions of the tissue, over
prolonged periods of time.
ssociation (c). (a) Bone is a composite material associating collagen fibers and
onsible for new matrix formation, in which they are later embedded and become
m of bone remodeling. (b) The orientation of the collagen fibers and chondrocyte
superficial zone, M: middle zone, D: deep zone, CC: calcified cartilage, SC:
8]).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 43
Throughout life, physiological remodeling, removal, and
replacement of bone, at roughly the same location, occur
without affecting the shape or density of the bone, through a
sequence of events that include osteoclast activation, resorption
of bone, osteoblast activation, and formation of new bone at the
site of resorption [28]. Bone remodeling patterns change
dramatically with the age and are illustrated by diseases such as
postmenopausal osteoporosis, which is characterized by bone
mass loss that enhances bone fragility and fracture risks. This
loss of bone density is a result from an imbalance between bone
formation and bone resorption related to estrogen deprivation
[29]. Another example is the modification of bone shape and
density of astronauts, who are subjected to zero-gravity for long
periods of time [30].
2.2. Self repair of hard tissues: example of smart materials
Bone possesses self-regeneration capacity. In fact, in
mammals, the complete reconstitution of a pre-injured state
is a unique feature for bone; all other tissues, with exception of
embryonic tissues, heal with the formation of a scar [31]. The
mechanism of bone regeneration is different than the one of
modeling and remodeling as it involves a preliminary blood
invasion – up to 1 L – at the injured site. The bone-healing
mechanism involves several phases and mechanisms. First,
blood cells (red blood cells and platelets) and fluid proteins
escape the damaged tissue and vessels. A protein-based
network composed of fibrin is formed. Second, through the
emission of signals from the fibrin network and surrounding
cells, other cell types are migrating towards the wound in order
to initiate the formation of early tissues (granular tissues). This
granulation mechanism consists of three phenomena, namely
(i) cellular clearance involving macrophages that remove
damaged entities, (ii) multiplication and invasion of other cell
types that initiate neo vascularization of the wound, and (iii)
early synthesis of a matrix composed of a network of several
proteins such as fibronectin, proteoglycans, hyaluronic acid and
collagen. A callus is formed consisting of cartilage. This
Table 2
Different types of cartilage
Type Where Main fu
Hyaline cartilage Articulating ends of bones Reduce
Trachea Movem
Larynx Suppor
Tip of nose Longitu
Connection between ribs and
Breastbone
Epiphyseal growth plate
Fibrous cartilage Intervertebral disc Shock a
Meniscus Provide
Impedin
Deepen
Disloca
Elastic cartilage Lobe of the ear Maintai
Epiglottis Suppor
Parts of larynx
cartilage hypertrophies and will eventually replaced by
bone. . .. In summary, when bone is injured, several cellular
mechanisms involving signaling, sensing and migration are
activated to reconstitute functional bone tissue. After a
complete healing process, bone shape and mechanical proper-
ties are entirely restored.
There is a limit to the size of fractures and defects that can be
self-repaired by bone. The upper limit is called the critical size
defect, and is defined as a defect of a size that will not heal
during the lifetime of the animal [32]. For larger defects, human
interventions are necessary to completely restore the defect.
3. Soft skeletal tissues
3.1. Structural and compositional organization of cartilage
Normal articular cartilage is hyaline cartilage, which is one
of three types of cartilage found in humans (Table 2). It is
located at the articulating ends of long bones and in the septum,
whereas elastic cartilage and fibrocartilage are located in the
epiglottis and ear, and intervertebral discs and cartilage
menisci, respectively [33]. Articular cartilage structure consists
of four adjacent, interdigitating and organized zones. These are,
from the tissue exposed to the synovial fluid in the direction of
the subchondral bone, the superficial-, middle-, deep- and
calcified zone. Chondrocytes in each zone have different
morphologies and the specific zonal tissue organization and
orientation play distinct roles in cartilage function and
metabolic activities (Fig. 1) [34].
3.1.1. Physical and chemical components
When hydrated, hyaline articular cartilage consists of
approximately 30% extracellular matrix (ECM) proteins,
whereas approximately 70% is water [35]. The ECM consists
predominantly of cartilage-specific proteoglycan (aggrecan)
molecules with highly negatively-charged sulfated glycosami-
noglycan (GAG) side chains, as well as type II collagen fibrils.
Other structural and attachment proteins are also present in
nctions (depending on tissue) Typical markers
s friction at joints Collagen type 2
ent Aggrecan
t Glycosaminoglycans (GAG)
dinal bone growth Chondroitin
Collagen type 10
(hypertrophic chondrocytes only)
bsorbers Collagen type 2
s sturdiness without Collagen type 1
g movement
s sockets to prevent
tion of bones
n shape Collagen type 2
t Aggrecan
Glycosaminoglycans
Chondroitin
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7144
ECM in low quantities, such as collagens type IX and, X,
fibronectin and Tenascin-C [34,36,37]. Chondrocyte hypertro-
phy results in a modified pericellular matrix, with increased
secretion of collagen type X and lower levels of collagen type II.
There is a developmental relationship between bone and
cartilage, with cartilage playing a role in the formation of long
bones in vertebrates by ‘endochondral ossification’, a process in
which bones are preshaped in cartilage that is gradually
replaced by bone except for the cartilage found at the
articulating ends of the bone, hence the term ‘articular
cartilage’ [38].
3.1.2. Cellular component
Chondrocytes are the only cell type found in normal articular
cartilage, and are mesenchymal in origin [39]. Chondrocytes
share a common progenitor with osteoblasts: the osteochon-
droprogenitor cell. Chondrocytes contribute to less than 2% of
the wet weight in healthy adult tissue [34]. Under non-
pathological conditions, these cells have a spheroid morphol-
ogy, 10–20 mm in diameter, and are connected to a densely
GAG-rich pericellular matrix.
3.1.3. Biological properties
In close association with bone, articular cartilage insures
joint lubrication and movement. The GAG side chains of
aggrecan are able to bind water molecules, thereby sequestering
water and generating an internal swelling pressure within the
cartilage matrix. These hydrogel-like properties are essential
for the interstitial fluid flow patterns observed inside the matrix
during functional loading of cartilage, at which point water is
forced out of the tissue to an amount that allows the negatively
charged GAG chains to repel each other [40]. Upon release of
the compressive load, water is imbibed back into the tissue
matrix. The collagenous network, together with water-bound
GAG, enables articular cartilage to withstand large compressive
loads which gives the tissue its unique function in the skeletal
system.
3.1.4. Intrinsic cartilage tissue repair
It has been long known that chondral lesions have limited
capacity for self-repair [41]. Like other tissues, cartilage will
undergo an initial phase of necrosis in response to injury, but
inflammation and subsequent vascularization is largely lacking
[42]. Only when the injury reaches the subchondral bone self-
healing processes are initiated by the release of blood-born
factors and mesenchymal progenitor cells from bone marrow
into the wound site. The drilling through to subchondral bone,
allowing the migration of bone marrow in the cartilage lesion is
frequently used to treat chondral defects [3,36]. However, the
resulting tissue is mostly fibrous and not hyaline cartilage. Not
surprisingly, it lacks the mechanical characteristics of normal
articular cartilage and has been reported to begin to degrade
within a few months of the procedure [43]. Other techniques,
such as microfracture and abrasion chondroplasty, also attempt
to utilize the release of progenitor cells and growth factors in
blood into the lesion. They also result in the formation of
fibrous cartilage [3,36,44].
4. Current strategies to repair skeletal tissues
The performance of tissues are the result of millions of years
of evolution, while the performance of the substitution that
mankind has designed to repair tissues are only a few decades
old. The main current strategies to repair tissue are:
(i) G
rafts: a piece of viable tissue or a collection of viablecells transferred from the donor site to a recipient site for
the purpose of reconstruction of the reconstruction site [1].
(ii) B
iomaterials: materials intended to interface with biolo-gical systems to evaluate, treat, augment or replace any
tissue, organ or function of the body [1].
(iii) T
issue engineering: the persuasion of the body to healitself, through the delivery to the appropriate sites of
molecular signals, cells and supporting extracellular
structures [1].
Biomaterials and grafts are widely used in clinical
applications, while tissue engineering is still at its infancy.
The current strategy in tissue repair is to design hierarchical
constructs able to (i) be accepted by the living body, (ii) restore
the damaged function, and more challengingly, and (iii) react in
a controlled manner with the biological environment in order to
stimulate specific biological mechanisms.
4.1. Biomaterials
Replacing body parts, and specifically hard tissues, dates
back centuries by the use of natural or synthetic materials. For
instance, the Etruscans learned to substitute missing teeth with
bridges made from artificial teeth carved from the bones of
oxen, and in the 17th century a piece of dog skull was
successfully transplanted into the damaged skull of a Dutch
duke. The Chinese recorded the first use of dental amalgam to
repair decayed teeth in the year 659 AD, and the pre-Columbian
civilizations used gold sheets to heal cranial cavities following
trepanation. However, many other implantations failed as a
result of infection or lack of knowledge about toxicity of the
selected materials.
The safe use of materials to replace body parts did not come
into practice until the advance of aseptic surgical techniques at
the end of the 19th century. For decades, attempts have been
made to repair or to replace hard tissues (bone and teeth) by
various means. At first autologous bone was used, but grafting
usually requires a second surgical procedure. To overcome this
shortage, allogeneic bone was taken into consideration, but its
clinical performance is inferior as compared with autologous
bone. In addition in load bearing applications, such as teeth or
hip implants, bulk grafts cannot be used functionally. Instead,
metals and non-degradable ceramics have been used because of
their resistance to fatigue and high tensile strength [45]. Until
the 1960s, materials used to replace body parts were borrowed
from other industrial domains, and some of these are still
widely used. Since the 1960s, materials specifically designed
for body repair have been processed and used in clinical
settings.
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 45
Regardless of their composition or application, materials
used for body repair must meet both biofunctionality and
biocompatibility. Biofunctionality concerns the ability of the
implant to perform the purpose for which it was designated.
These requirements are: (i) mechanical properties such as
tensile strength, fracture toughness, elongation at fracture,
fatigue strength, Young’s modulus; (ii) physical properties such
as density in the case of orthopedic implants, or thermal
expansion in the case of bone cement; and (iii) surface
chemistry such as degradation resistance, oxidation, corrosion,
or bone bonding ability [45]. Biocompatibility is defined as the
ability of a material to perform with an appropriate host
response in a specific application [1].
Various types of synthetic substitutes have been developed
in order to comply with biofunctionality and biocompatibility.
They belong to the following main material classes:
(i) M
etals such as titanium, titanium alloys, stainless steel,cobalt–chromium alloys.
(ii) C
eramics such as aluminum oxide, carbon, calciumphosphates, glass–ceramics.
(iii) P
olymers such as silicon, poly(methyl methacrylate), polylactide, poly (urethane), ultra high molecular weight poly
ethylene.
(iv) C
omposites such as ceramic coating on metal implants, orceramic-reinforced polymers.
The choice of one material above another will depend on the
application and the type of function that needs replacement.
Unfortunately, none of the existing biomaterials can meet all of
the requirements. For example, in the case of load bearing
applications (dental or hip implants), the mechanical require-
ments are only met by metals. In particular, titanium alloys are
very promising in orthopedics due to their high specific
strength and low elastic modulus [46]. Titanium exhibits a
strong tendency towards passivation and rapidly forms an
oxide film in the presence of oxygen. Within a millisecond of
exposure to air or aqueous solution, an oxide layer of 1 nm in
thickness will be formed on the surface; and within 1 min, the
oxide film is about 5 nm. This oxide film is very adherent and
stable, and does not break down under normal physiological
conditions. Because of this fast spontaneous formation, there is
no direct contact between the titanium and the host tissue;
instead, they are separated by this thin layer of surface oxide.
The corrosion resistance of titanium towards biological
environment is provided by this protective oxide film [47].
However, titanium has a limited bone-bonding activity
compared to other materials such as calcium phosphates
which have strong bone-bonding capacity but unsatisfactory
mechanical properties (see Table 3).
4.2. Cell-based therapies
In contrast with bone, repair strategies for soft tissue repair
are mainly based mainly on grafts or cell therapies. In articular
cartilage, for example, the most common defects are either
contained within the layer of cartilage articulating the ends of
long bones, or penetrate deeper through the cartilage into the
subchondral bone [3,48]. They are formed due to joint diseases
such as osteoarthritis (OA), rheumatoid arthritis (RA), genetic
and metabolic conditions such as Paget’s disease or from
trauma to the joint [49,50]. Although all the origins of OA have
not completely been identified, it is known that lesions can
ultimately lead to OA. It is, however, not certain that lesions
always are the cause of OA. When OA does arise from
structural damage to the articular cartilage matrix, it does so by
the production of degradative enzymes including a series of
matrix metalloproteases (MMPs) by chondrocytes that results
in the release of proteoglycans from the ECM and erosion of the
collagenous network in cartilage due to an imbalance between
anabolic synthesis and catabolic proteolysis [3,51,52]. It has
also been demonstrated that chondral lesions left untreated for
extended periods (6 months, according to some clinical studies)
may result in joint instability causing the onset OA [50,53–55].
Autologous tissue transplantation can take the form of
‘‘mosaicplasty’’, in which osteochondral plugs from non- or
low-loading regions of the articulating surface are harvested
and transplanted to fill the defects [3,44,56]. However, lack of
suitable donor tissue and donor site morbidity limit the scope of
this technique. Mosaicplasty has also been performed with
allogeneic (cadaveric) osteochondral plugs, although there are
concerns about immunogenic response and the potential for
transfer of infectious diseases. Other tissue transplantation
procedures include the grafting of periosteum and perichon-
drium to defect sites in the articular tissue. In these techniques,
progenitor cells in the cambium are believed to be induced
towards chondrogenesis [36,57]. However, these procedures
fall short of satisfactory functional and histopathological repair
in long term studies due to a number of reasons, including the
lower chondrogenic potential of resident precursor cells in
older patients, who comprise most clinical cases [54,58].
However, it has also been reported that periosteum derived cells
maintain sufficient potential for chondrogenesis for all ages
assessed, if cultured in micromass with the inclusion of TGF-
b1 [59].
Although evaluated in rabbit models as early as 1971 [60],
the implantation of autologous expanded cells in suspension
has seen some growth since the first reported clinical study in
1994 [61–63]. In this procedure, chondrocytes isolated from
articular cartilage biopsies are expanded in vitro prior to being
resuspended in culture medium and injected into the defect site.
The defect is closed with a periosteal flap fixed with sutures to
prevent cells from escaping. However, in vivo studies have
yielded conflicting results. It is as yet unclear whether it is the
transplanted chondrocytes or progenitor cells in the periosteal
flap that are responsible for differences, if any, with respect to
empty defects [64]. Although cell persistence has been reported
[65], there is some uncertainty as to whether the cells remain
within the lesion, since the periosteal flaps have been shown to
detach within a few days after suturing [66]. Some clinical long
term follow-up studies have reported improved outcomes for
treated, as compared to untreated lesions, although in some
cases long recovery times have been cited as drawbacks [61–
63,67,68].
Table 3
Biomaterials clinically used in musculoskeletal repair in the US or Europe
Composition Type Origin Clinical applications Properties
Calcium phosphate,
i.e. hydroxapatite;
tricalcium phosphate;
octacalcium phosphate
Ceramic Synthetic Bone regeneration, non-loading
sites, bone void filler
(cements, granules, coatings)
Bone bonding (bioactivity),
biodegradable, tunability
of degradation
Silica-based calcium phosphate Glass ceramics Synthetic Bone regeneration, non-loading
sites, bone void filler
(granules, coatings)
Bone bonding (bioactivity),
Biodegradable
Alumina Ceramic Synthetic Joint replacement (knee, shoulder) Highest tensile strength,
resistance to fatigue,
non-bone bonding,
lubricating capacity
Titanium and alloys Metal Synthetic Bone replacement, load-bearing
sites, hip or dental prosthesis,
spinal cages
Bone bonding (bioactivity) in
some cases, non-corrosive,
resistance to fatigue, high
specific strength, low elasticity
modulus
Stainless steel Metal Synthetic Bone replacement Corrosive to long term
Cobalt chrome alloys Load-bearing sites, hip or dental
prosthesis, spinal cages, fixations
Polymethylmethacrylate Polymer Synthetic Bone replacement, load-bearing sites,
bone void filler (cement) fixation
of hip prostheses, vertebroplasty
Non-degradable
Polyesthers, i.e. poly lactide,
poly glycolic acid, poly
caprolactone, poly (urethane)
Polymer Synthetic Degradable bone fixation, soft tissue
suture, bone void filler, soft tissue
regeneration*, drug delivery*
Tunability by varying molecular
weight of degradation and
mechanical properties
Ultra high molecular weight
poly ethylene
Polymer Synthetic Articulating component for
orthopaedic prosthesis, load
bearing sites
Lubricating capacity
Poly poly ethylene oxide
terephtalate co
butylene terephtalate
Co-Polymer Synthetic Cement stopper, bone void filler, soft
tissue regeneration*, drug delivery*
Tunability by varying molecular
weight of degradation and
mechanical properties, bioactivity
Polyphosphazene Polymer Synthetic Drug delivery* Erosion degradation mechanism
favorable to long term stability
of the implant
Polyanhydride Polymer Synthetic Drug delivery, hard and soft
tissue repair*
Erosion degradation mechanism
favorable to long term stability
of the implant
Poly ortho esters Polymer Synthetic Food additive, drug delivery*,
hard and soft tissue repair*
Poly ethylene glycol Polymer Synthetic Drug and cosmetic excipient,
hard and soft tissue repair*
Injectable water gel,
degradable
Coral Mineral Natural (sea) Bone void filler High interconnectivity,
degradable
Bone Composite
mineral/proteins
Natural
(human, bovine)
Bone void filler Similar composition as the
host bone
Demineralized bone matrix Proteins Natural (human) Bone void filler, cartilage regeneration* Biodegradable, natural source
of osteoinductive
proteins (BMPs)
Collagen Protein Natural (bovine) Hard and soft tissue repair Biodegradable
Hyaluronic acid Polysaccharide Natural (human) Soft tissues repair Biodegradable, injectable
hydrogel, naturally abundant
in joint synovial fluids
Alginate Polysaccharide Natural (algae) Soft tissue repair Drug load, degradable
Agarose Polysaccharide Natural (algae) Soft tissue repair* Drug load, Degradable
Chitosan Polysaccharide Natural
(sea crustaceans)
Soft tissue repair Structurally similar to
glycosaminoglycans
(cartilage proteins)
Fibrin Protein Natural (human) Soft tissue healing, bone void filler Sealing capacity
(*) Indicates potential future clinical applications based on preclinical data.
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7146
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 47
To date, both the use of either biomaterials or cells alone is
not sufficient to comply with the highly complex and hierarchal
requirements of our body. We are forced to innovate new and
smarter ways to instruct bodies to heal.
4.3. Towards smart designs to repair tissues
4.3.1. Biomimetic materials for skeletal repair
Learning from nature, in order to synthesize its ‘‘products’’,
is a challenge. In tissue regeneration, nature offers examples of
smart, adaptive and ‘‘strong’’ materials, inspiring us to
synthesize similar performing products, commonly referred
to as biomimicry. The concept of biomimicry is quite novel in
the biomaterials field, but it has been used implicitly for much
longer, in different ways and for diverse purposes [69]:
(i) F
unctional biomimetism is the primary goal in designingbiomaterials where tissue function should be restored. For
example, a biomimetic hip prosthesis should restore the
function of a healthy hip with a very low friction
coefficient between the femoral head and the acetabulum
and with a high resistance to mechanical load (compres-
sion, elasticity).
(ii) M
aterial biomimetism, where restoration of the organfunction is assumed to be obtained if the tissues themselves
are imitated. For example, calcium phosphate ceramics
have been successfully proposed as bone substitutes
because of their chemical similarities with bone mineral
[69].
(iii) B
iological biomimetism, where restoration of the tissue issynthetically stimulated by implanted cells or molecules
that are involved naturally in the mechanisms of tissue
formation or function.
4.3.1.1. Biomimetic biomaterials for hard tissues. Regarding
bone substitution, the biomimetic synthesis of biomaterials is
based on bone biomineralization that can be described as an
extracellular precipitation under physiological conditions of pH
and temperature. The nucleation and crystal growth are
controlled by (i) spatial delineation by supramolecular
assemblies, (ii) chemical regulation by transport processes,
and (iii) molecular recognition at inorganic–organic interfaces
[74]. It offers several advantageous alternatives in favor to bone
repair. As calcium phosphate ceramics are brittle [75], a bone-
like composite prepared under mild conditions, and composed
of an organic matrix and mineral crystal would open the
possibility to use these bioceramics in load-bearing applica-
tions. Additionally, a mineral phase synthesized under similar
physiological conditions to bone mineral might confer to the
ceramic a reactivity that could positively influence cells and
hosting tissues in favor to new bone formation. Indeed, the
biological apatitic crystals are highly reactive due to their
hydrated, poorly organized outer surface [20,76,77]. In
particular, the presence of non-apatitic phosphates in these
biological crystals affect their biological properties [76]. In that
sense, any calcium phosphate ceramic obtained by a classical
process involving high temperature cannot imitate this very
specific reactivity. The biomimetic synthesis of calcium
phosphate biomaterials under physiological conditions can
lead to new calcium phosphate ceramics with very different
physico-chemical properties, affecting their reactivity towards
the biological surroundings. The biomimetic method has been
explored and led to coatings on implants substrates or powdery
compounds.
Simulated body fluids (SBF), supersaturated with respect to
apatite, have been developed and used to synthesize ‘‘bone-like
crystals’’ and other calcium phosphate phases that are
considered bone mineral precursors [14,78,79]. As with bone
mineral deposition, this biomimetic process requires an
heterogeneous substrate onto which nucleation and crystal-
lization will occur over time from fluids supersaturated with
respect to apatitic phase [80]. Some strategies have been
developed to synthesize the biomimetic biomaterials by:
(i) C
hemical regulation by transport processes from syntheticextracellular fluids, such as simulated body fluids [81] and
derived solutions [82–84]. This synthesis led to the coating
of various biomaterials in order to enhance their bone-
bonding ability [85–87]. More interestingly, biomimetic
synthesis opens broad new possibilities for biomaterials
functionalization. First, the deposition of calcium phos-
phate layers on porous and/or thermosensitive scaffolds
triggering bone formation, ingrowth and contact with the
implant [87–90]; second, the co-precipitation of organic
molecules like the osteoinductive bone morphogenetic
protein (BMP-2) or antibiotics [91–93], third, a fine control
of the surface physicochemistry at the molecular and nano-
metric scale that can influence in vitro and in vivo the
biological response [78,94].
(ii) M
olecular recognition at inorganic–organic interfaces. Thegrafting of specific functions onto biomaterials stimulating
self-assembling of ions have been explored [95,96]. In both
cases, nucleation and crystallization mechanisms were
enhanced by using biomimetic principles. Chemical
regulations by transport processes and spatial delineation
by supramolecular assemblies have been also exploited for
the synthesis of bulk biomaterials. As such, these strategies
led to the formation of powdery samples [97]. No bulk
biomimetic biomaterials could be produced in the size
range of ‘‘classical’’ bone biomaterials (from circa
0.125 cm3 and bigger). However, with the aid of modern
techniques such as rapid prototyping or free-form
manufacturing bulk bioceramics with complex shapes
and relevant sizes can be nowadays obtained [98,99].
4.3.1.2. Biomimetic biomaterials for soft tissues. Polymers
can also be fused with bioactive peptides to create biologically-
responsive hydrogels. This concept has been illustrated for the
repair of various tissues, including bone [100–104] and
cartilage [105]. This approach seeks to mimic the tissue
extracellular matrix with hydrogel matrices that incorporate
various biological signaling moieties, such as arginine–
glycine–aspartic acid (RGD) peptides or laminin-derived
peptide IKVAV, or linkers that are susceptible to cell-secreted
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7148
proteolytic factors, such as MMPs or plasmin [106–110]. These
quasi-ECMs allow for the spatial as well as temporal regulation
of cell migration and matrix degradation that is uniquely
determined by the cells contained within the gels. These are
man-made examples of bidirectional signaling between cells
and their ECM, that mimic (to a lesser extent) signaling from
the ECM to the cell (outside in) and vice versa (inside out), that
are crucial in maintaining cell viability, phenotype, migration
and production of ECM proteins. Specific examples include
poly(ethylene glycol)-bis-vinylsulfone polymers containing
peptide sequences with three cysteine residues [111]. In this
system, cell invasion in the hydrogel occurred when the
network was crosslinked by plasmin-sensitive peptides and
contained cell adhesion peptides. Conversely, hydrogel net-
works lacking either of these features did not allow cell
infiltration. PEG and N-(2-hydroxypropyl)-methacrylamide
(HPMA) are often used as physical or chemical crosslinkers,
with PEG impacting the physical properties of the hydrogel
[112].
The fibrillar architecture of the ECM has lead to the design
of polymers that mimic scale, topography and shape. These
structures can now be fabricated at the nanometer scale, which
is essential for providing signals to cells that mimic the natural
biological microenvironment. Techniques used for these
include electrospinning and molecular self assembly based
on non-covalent interaction between amphiphilic peptides,
synthetic polymers or oligonucleotides, and have been used to
demonstrate control of biologic function in chondrocytes, liver
hepatocytes and neural cells [113–117].
Biomimetic synthesis is an emerging promising field that
needs to demonstrate clinical benefit over ‘‘classical’’
approaches.
4.3.2. Tissue engineering
The last two decades have seen a surge in creative ideas and
technologies developed to tackle the problem of repairing or
replacing diseased and damaged tissues, leading to the
emergence of a new field in healthcare technology now
referred to as tissue engineering. It has been defined by some as
‘‘an interdisciplinary field that applies principles and methods
of engineering and the life sciences toward the development of
biological substitutes that restore, maintain and improve the
function of damaged tissues and organs’’ [118].
The earliest tissue engineering strategies were reported for
the delivery of encapsulated beta-islet cells in diabetic patients
(1975) [119], dermal regeneration by applying a glycosami-
noglycan-collagen composite matrix over burn sites (1980)
[120] and a collagen matrix impregnated with fibroblasts to
also aid in skin repair and regeneration (1983) [121]. This was
followed by the development of porous synthetic polymer
scaffolds to deliver cells and neo-tissue, a strategy that has
since then been evaluated for most tissues [122,123]. For
example, tissue engineering strategies for repairing different
tissues such as cartilage [3,50,52], bone [12,56,124], tendon
[125,126], liver [127], cardiac muscle [128–130] and neural
tissue [131,132] have been described and reviewed elsewhere
in detail.
The modern concept of tissue engineering draws on multiple
areas of expertise. It is a convergence of the fields of materials
science and engineering, cellular and molecular biology,
biochemistry, controlled release systems for biotherapeutics,
and surgery. Briefly, cells are removed from a patient via a
tissue biopsy performed by a surgeon or physician. Once, after
cell expansion, a sufficient number of cells have been reached
for the intended application, they are transplanted back into the
patient using either natural materials, synthetic polymers,
ceramics, or composites for cell delivery. These three-
dimensional structures can be formed in the shape of the
defect to be replaced, or be delivered as injectable gels to fill the
defect site in situ. They allow cells isolated from the biopsy to
produce the structural proteins found in the original tissue, such
as collagen. The neo-tissue can be grown in vitro in the scaffold,
eventually reaching a stage where it is suitable for implantation
back into the patient to replace damaged or diseased tissue or be
allowed to grow in situ within the defect. Fig. 2 schematically
illustrates an example of the tissue engineering process.
Recent advances in materials science, including photo-
polymerizable gels and ‘‘smart’’ materials that can change
surface chemistry based on the local electro- and biochemical
environment have greatly added to the options available to
tissue engineers [133,134]. On the other hand, rapid progress in
our understanding of the cellular and molecular events involved
in the natural development of tissues, such as those that occur
during the ultimate example of tissue engineering – the
embryonic development of the fetus – have opened the
possibility for therapy using pluripotent stem cells [79,135–
137].
In spite of the rapid developments taking place, the field of
tissue engineering is still in its infancy. The only true
commercially available products at this point are skin grafts
and cartilage repair procedures. However, this technology is
likely to benefit as further convergence of nanotechnology,
proteomics, gene therapy and stem cell research allows tissue
engineers to repair and perhaps regenerate tissues and organs,
with the potential to greatly improve the lives of people with
functional disabilities [138].
4.3.3. Materials for tissue engineering
Materials selected for tissue engineering must interact with
cells and culture media in vitro prior to their implantation. In
addition, these scaffolds and matrices, have to (i) host a
sufficient amount of cells and (ii) support their viability for
several weeks. Scaffolds refer to solid porous structures, while
matrices refer to gel-like structures.
4.3.3.1. Natural materials. Nature offers several potential
sources of materials for tissue regeneration scaffolds. Although
they have been shown to support cell viability and tissue
formation to various degrees, natural matrices such as
hyaluronan (hyaluronic acid) and fibrin are unable to endure
body’s loading conditions. Furthermore, the defect borders may
degrade if the defect is not filled with an implant of similar
mechanical properties [55], and esterified hyaluronan and fibrin
have sometimes demonstrated undesirable effects on the host
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 49
tissue and its repair [139–142]. Another group of natural
polymers that have been investigated for this purpose comprises
polysaccharides like alginate [143,144] and chitosan [145,146].
These materials have been studied for cartilage and skin
regeneration [147–149] and reached clinical applications for
the treatment of deep skin wounds and cartilage [150,151].
Chitosan has satisfactory biocompatibility, but mechanical
loading issues remain [152]. Agarose, alginate and collagen
hydrogels have been studied for their potential as injectable
materials in which chondrocytes or precursor cells can be
Fig. 2. Diagram representing current tissue engineering strategies. (a) Cells are ha
proliferate in vitro prior to (c) seeding in 3D scaffolds, and cultivated in bioreactor
prepare scaffold consists of design via 3D computer aided technique from a 3D-CT s
fibre deposition can realize bulk scaffolds (herewith an articular joint). (e) The final c
takes place.
mixed or embedded. Alginate consists of two repeating
monosaccharide units, L-gluronic and D-mannuronic acids,
which are water soluble and jellify when exposed to calcium
ions. Chitosan is structurally similar to glycosaminoglycan
(GAG) and is composed of b linked D-glucosamine residues. It
has been recently attracted more and more attention because of
its non-toxicity, bioresorbability, and wound healing abilities
[153]. Hyaluronic acid is also abundantly present in the human
body articulation, within the synovium fluid. However, in its
natural form this material lacks some desirable properties (too
rvested from tissue and isolated in vitro. (b) These cells can then be made to
conditions to produce viable constructs. (d) The most sophisticated strategy to
cans of the body part to be replaced. Solid free-form fabrication, including 3D-
ell-scaffold construct is implanted back into the patient, where tissue formation
Fig. 2. (Continued ).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7150
high water solubility, fast resorption and tissue clearance times)
to consider it as a polymer for scaffold fabrication [154]. A
change of its chemical structure through an esterification
reaction allows the generation of a new set of biomaterials,
hyaluronan, with improved properties, increased biocompat-
ibility and fine-tunable degradation rates [155,147,156].
Although these materials allow tissue formation within the
gel, they too are limited with respect to the mechanical loads
they are able to withstand. Collagen has also been studied in
cross linked, hardened gel and lyophilized states, with some
success [157–159] and for various tissue regenerations [160–
164]. In particular crosslinked collagen type I and type II
scaffolds alone, or in combination with glycosaminoglycans
have been considered for bone and cartilage repair [163–166].
However, their gel nature seems to prevent the cell migration
within the matrix, reducing so the tissue repair [61]. A further
possibility is to use denatured collagen (gelatin) [161], fibrin
[167,168] or demineralized bone matrix (DBM) [169–171].
DBM is the organic phase of bone tissue after thorough
demineralization processing. The bioactive proteins, namely
bone morphogenetic proteins (BMPs) and some other growth
factors that are bound to the extracellular collagen matrix, are
Fig. 2. (Continued ).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 51
made more available to the surrounding tissues [172]. However,
the demineralization process can affect strongly the proteins
conformation and also the organic matrix tri-dimensional
organization, affecting therefore the osteogenic potential of
these compounds [173]. Natural minerals, such as coral- and
bovine bone derived materials are also used in bone tissue
engineering; they provide an efficient porosity and intercon-
nectivity for cell and nutrient penetration in combination with
elevated mechanical properties.
4.3.3.2. Synthetic materials. Several materials and matrices
have been evaluated for tissue engineering purposes [3,48].
However, there are considerable issues associated with the
choice of carrier matrix, among which are biocompatibility of
the material, its degradation products and the ability of the
matrix to withstand mechanical loading. Biomaterial properties
that influence cell behavior are addressed in later this review.
Synthetic biomaterials containing calcium and phosphate
groups, such as calcium phosphate ceramics and calcium
phosphate silica glasses (or bioactive glasses) exhibit excellent
bone-bonding properties that are related to the surface
reactivity, via dissolution–precipitation mechanisms. In addi-
tion, they degrade naturally: the degradation products are
entirely metabolized in a natural way by our bodies [70,71].
These bone-bonding and degradation features are unique and
have contributed to their clinical success for 40 years [72,73].
The first clinical attempt to use calcium phosphate compound
was in the successful repair of a bony defect reported by Albee
in 1920 [73]. Since then, several calcium phosphate biomater-
ials have been developed and successfully applied in the clinic,
such as hydroxyapatite, tricalcium phosphate, bicalcium
phosphate, brushite and octacalcium phosphate. As porous
structure they are good candidates as scaffolds for bone tissue
engineering.
Synthetic polymer hydrogels have shown promise as
injectable gels and for embedding chondrocytes, although
their use too has been limited by biocompatibility issues and
often low mechanical stability under loading [3,48]. In
addition, hydrogels are not favorable to migratory cells often
used in bone tissue engineering [174]. But advances in polymer
technology have enabled these issues to be addressed, while
preserving their beneficial features [175]. Furthermore, these
advances have also enabled the generation of hydrogels that are
photopolymerizable, pH and thermoresponsive [133,176]. The
polymers most extensively tested for connective tissue repair
belong to the poly(a-hydroxy esters) family and include
poly(glycolic acid) (PGA), poly(lactic acid) (PLA) and their
copolymers (PLGA), with much of the focus on non-woven
PGA fiber meshes since this polymer was shown to support
improved cartilage matrix and tissue formation over PLA or
PLGA [177–183]. However, these polymers biodegrade to
produce acidic degradation products that can have adverse
effects [184,185]. Additionally, a key issue in tissue engineer-
ing is the ability of the tissue engineered construct to integrate
with the surrounding tissue at the defect site. This is an
especially relevant point in situations where relatively mature
cartilage tissue has been grown in vitro prior to construct
implantation. An approach to deal with this issue is to
transplant constructs with less mature tissue at an earlier stage,
with the reasoning that most of the tissue formation should
occur in situ and thus enable better integration with the
surrounding host tissue [186]. However, the lack of mechanical
stability of fibrous PGA as described earlier precludes their use
in applications in which chondrocytes, or progenitor cells, are
to be transplanted to defects at an early stage. Composite PLGA
scaffolds reinforced with PGA fibers have also been designed
and evaluated to compensate for shortcomings of the individual
components, with success in in vivo osteochondral defect
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7152
models [187,188]. A recent study using expanded chondrocytes
cultivated on hyaluronan scaffolds for the repair of articular
cartilage lesions demonstrated considerably positive results in
terms of histology and biological acceptability of neo-tissue as
well as functionality and patient quality of life [68].
Despite the apparent simplicity of this single cell-type
tissue, it is clear that current techniques for repairing skeletal
tissues are frequently unsatisfactory, requiring the develop-
ment and implementation of novel technologies and
procedures for achieving the desired clinical objectives.
Among the techniques under development for repairing
damaged tissues is the immobilization and transplantation of
cells on carrier scaffolds, or tissue that has been grown in
vitro, to fill defect sites. Cells (mostly autologous, although
allogeneic sources have also been studied) can then be seeded
either directly onto carrier scaffolds, or be proliferated in vitro
prior to seeding onto scaffolds, with the latter case being more
realistic due to the limited number of cells that can be
harvested from tissue biopsies. Depending on the length of
culture and cultivation conditions, tissues may be grown to
varying degrees within the carrier scaffolds prior to
implantation into defect sites [3,48,52,56,68,189]. To that
end, extensive research has been done in evaluating a range of
cell sources, materials for cell transplantation as well as
scaffold designs that can be used to immobilize cells and
support neo-tissue synthesis.
Among the strategies developed to improve tissue engineer-
ing therapies, selecting, designing and engineering scaffolds
and matrices are of utmost relevance. Depending on their
intrinsic properties, such as surface properties and porosity,
some biomaterials have shown interesting instructive properties
with regard to tissue formation.
5. Instructing physico-chemical and biological
processes at biomaterial interfaces
There is a great gap in the complexity, hierarchy and
intelligence between tissues and their potential substitutes. A
detailed understanding of the interactions between biomater-
Fig. 3. Physico-chemistry of the biomaterial in con
ials, cells, fluids and tissues is mandatory. With this knowledge,
we will be able to engineer smarter materials capable of
instructing their biological milieu for a complete tissue
regeneration.In vivo, the interactions between the implant
and its ‘‘biological surrounding’’ occur in non-equilibrium
conditions (Fig. 3). The amount of compounds playing a role in
these interactions remains undefined. Regardless the nature of
the biomaterial, its biological surrounding evolves with time.
For example, Dhert et al. have described the events taking place
between different biomaterial implants in contact with the host
bone. In the first 3 days, blood invaded all of the empty
interstitial space between the host bone and implant. At the end
of the first week of implantation, callus and mesenchymal
tissues entirely replaced blood, concomitant with host bone
resorption. Finally, between the second and fourth weeks of
implantation, callus, mesenchymal tissues and host bone
gradually disappear in favor of newly formed bone while bone
remodeling takes place [205].
The following sections will review the newest concepts on
how to design smart implants for hard and soft skeletal tissues.
5.1. Osteoinductive biomaterials
A first striking example is relative to osteoinductive
biomaterials. In non-bone sites, some synthetic materials have
shown the ability to induce bone formation (osteoinduction) as
illustrated in Fig. 4c. At a first glance, the ability of a material to
form bone in a non-bony environment may not be relevant in
bone tissue regeneration. However, it has been recently
demonstrated that osteoinductive biomaterials stimulate more
bone formation when used as tissue engineered constructs in
goat muscle [209] as well as in critical size orthopedic defect
models in goats [210]. Therefore understanding osteoinduction
mechanism by biomaterials could offer a useful tool to repair
large bone defect.
Polymeric, metallic and ceramic biomaterials have shown
osteoinductive properties. In 1969, polyhydroxyethylmethyl-
methacrylate (poly-HEMA) sponges were reported to induce to
form bone in soft tissues [211]. In the last decade, calcium
tact with biological milieu (in vitro or in vivo)
Fig. 4. Bone-instructive implants. (a, b) Back-scattering electronic microscopy picture of an calcium phosphate coating (OCP) coating on a metallic porous scaffold
implanted for 12 weeks in the femoral condyle (goat) at different magnification (scale bar (a) 50 mm and (b) 10 mm). Between the OCP and the newly formed bone, an
interfacial phase (arrow) that can be attributed to superficial phase transformation is clearly visible. (c) Light-micrographs of a macroporous osteoinductive scaffold
(BCP) implanted in goat muscle for 12 weeks representing ectopic bone (dark grey) (magnification �20) (courtesy P. Habibovic).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 53
phosphates [85,210,212–222], alumina ceramics [223], tita-
nium [197,224] and glass ceramics [225] were also found
osteoinductive in soft tissues of different animals. Although the
mechanisms of osteoinduction by materials remain unclear,
critical physico-chemical factors of the biomaterials have been
identified: the macroporosity (pores larger than 10 mm), the
surface physico-chemistry, and the microporosity (pores
smaller than 10 mm) [210].
Regardless of their composition, all osteoinductive biomater-
ials exhibit macropores, whether they are initially present such as
macroporous structures [197,211,214,215,222,223,225,226] or
formed during the biomaterial’s degradation process (for
example, crevices at the surface of calcium phosphate cements)
[212,217]. Macropore geometry and tridimensional organization
are important criteria. Among several well-defined cavities
created on hydroxyapatite, only specific concavities were shown
to induce bone formation [226]. A comparative study between
two different macroporous structures of the same titanium
showed that only the complex tridimensional one was
osteoinductive while a regular fiber mesh did not induce bone
formation [197].
Osteoinduction has been found among various biomaterials
exhibiting very different surface properties. For example, the
calcium phosphates and bioactive silica glasses are known to
undergo surface transformation via a dissolution–reprecipita-
tion process favorable to bone-bonding. These ionic exchanges
properties of the calcium phosphate scaffolds with the
surrounding milieu have been pointed out as a relevant
parameter among others [210,215]. Titanium and poly (HEMA)
materials possess also the ability to nucleate a calcium
phosphate layer in vitro and in vivo [211,227–230]. This
calcification property has been proposed to be a precursor in the
osteoinduction mechanism [222]. However, alumina ceramics
that have been reported osteoinductive [223] are well-known
for their poor calcium phosphate nucleation ability [190,231].
They are used as knee joints because of their long-lasting
lubricant properties related to their resistance to calcification.
In addition, under physiological conditions of pH and
temperature, alumina surfaces are positively charged, while
titanium and calcium phosphate ceramics are slightly
negatively charged. These differences in surface charge will
also affect the interaction pattern with organic molecules
presents in the body fluids [232,233] and with cells. In view of
these large physico-chemical differences among the surfaces of
osteoinductive biomaterials, several different phenomena may
intervene in parallel.
By implanting intramuscularly in goats two macroporous
calcium phosphate scaffolds identical in composition, crystal-
linity and porosity but with different microporosities (pores
smaller than 10 mm), Habibovic have demonstrated that an
elevated microporosity was responsible for ectopic bone
formation [210]. This high microporosity is directly correlated
to roughness and exposed surface, and therefore reactivity.
Other types of osteoinductive biomaterials also exhibited an
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7154
elevated microporosity that may be responsible for triggering
cell differentiation towards the osteogenic lineage. In addition,
at specific surfaces, greater ionic and molecular exchanges
occur between the biomaterial and the biological milieu. A high
concentration of specific molecules (for example, osteoinduc-
tive BMPs), adsorbed directly at the biomaterial surface or co-
precipitated into the newly formed calcium phosphate layer,
favor bone formation [226].
Osteoinductive materials for bone demonstrate that bioma-
terials can specifically instruct the body to heal by itself.
Thorough studies have been conducted in order to study the
specific factors affecting these bone-instructive properties.
Osteoinduction mechanism remain unraveled but it has led to
the recognition of several biomaterials parameters that can be
tuned in order to guide the biological response.
The following section will detail the different parameters
affecting hard and soft skeletal tissue formation, and the smart
designs that have been derived from these.
5.2. Orchestrating biomaterials degradation with new
tissue formation
In the presence of fluids and cells, biomaterials undergo
degradation. In other words, their chemical structure, physical
properties, or appearance change [1]. The degradation
mechanisms depend on the nature of the biomaterials. While
calcium phosphate and bioactive glasses degrade by dissolution
and cellular (osteoclastic) mechanisms, polymers degrade by
chain scission, erosion and metabolization mechanisms [234].
5.2.1. Degradation mechanisms
5.2.1.1. Ceramics. In contact with biological fluids, calcium
phosphate ceramics degrade via dissolution–reprecipitation
mechanisms [203]. Ionic transfers occur from the solid phase to
the aqueous liquid via surface hydration of calcium, inorganic
phosphate species, and possible impurities like carbonate,
fluoride or chloride present in the biomaterial. Under
physiological conditions, this dissolution process is highly
dependent on the nature of the calcium phosphate substrate and
their thermodynamic stability, for example (in order of
increasing solubility), hydroxyapatite (HA) > tricalcium phos-
phate (TCP) > octacalcium phosphate (OCP) > bicalcium
phosphate dihydrate (DCPD) [190,194,199,235–238]. The
composition and supersaturation of the environment in vitro
[239–241], or the implantation site in vivo [242,243] also
influence the dissolution–reprecipitation mechanism. Ionic
transfers occur also from the surrounding fluids to the calcium
phosphate substrate in vitro and in vivo, as illustrated by the
formation of carbonated apatite nanocrystals as a result of
surface transformation [190–194,242,244] (Fig. 4a and b). The
presence of magnesium and carbonate contributes to the
formation of a poorly crystallized carbonated apatite that has
similar features with bone mineral phase [245–247]. In the
presence of proteins, this newly formed mineral phase is also
associated with organic compounds [190,192,195]. This phase
transformation occurs for all of the calcium phosphate
bioceramics, even the stable apatitic structures since they have
a strong ability to adapt to their environment by hosting foreign
ions and subsequently to undergo atomic rearrangements [20].
However crystalline hydroxyapatitic substrates are often too
stable to transform. The result of these ionic exchanges
favoring either phase transformation or dissolution follows
thermodynamic stability. This surface reactivity has pivotal
implications in the development of instructive functions,
namely osteoinduction and drug delivery systems. This will
be elaborated on later in this review.
5.2.1.2. Polymers. Biocompatible polymeric biomaterials
have also the potential to degrade in contact with biological
fluids [248]. Briefly, linear aliphatic polyesters such as
poly(lactic acid), poly(glycolic acid) and copolymers have
been broadly used, and their degradation rate can be tailored by
varying their copolymer ratio [249–253]. Their degradation
products (lactic and glycolic acids) obtained by hydrolysis are
normally present in the metabolic pathways of the human body.
However, their bulk degradation leads to the build-up of acidic
degradation products inside the matrix lowers the pH within the
polymeric matrix. This might result in local inflammation in
tissues if clearance of degradation products is insufficient [254].
Another family of thermoplastic polymers that has been
recently studied for bone and cartilage repair and regeneration
in view of tunable degradation properties is poly(ethylene
glycol)-terephthalate–co-poly(butylene terephthalate) (PEGT/
PBT). These polyether-ester multiblock copolymers belong to a
class of materials known as thermoplastic elastomers which
exhibit good physical properties like elasticity, toughness and
strength [92] which are critical for reconstructing load-bearing
tissues. By varying the molecular weight of the starting PEG
segments and the weight ratio of PEGT and PBT blocks it is
possible to tailor their biodegradation rate [255]. Being
polyether-esters, degradation occurs in aqueous media by
hydrolysis and oxidation, the rate of which varies from very low
(high PBT contents) to medium and high (larger contents of
PEGT and longer PEG segments) [92,255]. Among the
multitude of other synthetic polymers investigated for tissue
regeneration, interesting classes are polyphosphoesters [256],
polyphosphazenes [257–260], polyanhydrides [261] and poly-
ortho-esters [262].
5.2.2. Smart degradation designs
Controlling the degradation kinetics of biomaterials to
match tissue growth, to create space for the new tissues to grow
until full regeneration is reached remains a challenge in
biomaterial design. However, tools to tune the degradation
mechanism in favor to tissue regeneration are now becoming
available to researchers.
In large defects which cannot be healed naturally by bone,
adjusting the degradation kinetics of the calcium phosphate
bone filler to the kinetics of bone formation rate is possible by
changing the calcium phosphate phases of the biomaterials.
Mixing at various ratios a low soluble phase (HA) with a highly
soluble phase (amorphous, TCP) resulting in biphasic calcium
phosphates ceramics (BCP) [202,263,264], including additives
(magnesium, carbonate, fluoride) in a given crystalline phase
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 55
[190,199,265], or selecting different calcium phosphate phases
(amorphous, DCPD, OCP, HA, TCP) [190,265] are the options
to tailor the degradation kinetics of calcium ceramics, ranging
from weeks to years.
In view of the dissolution tunability of calcium phosphates,
several groups have used these ceramics as delivery systems for
gene [93] or drugs [91,92,266,267]. Drug association with
calcium phosphates can be performed by (i) adsorption on
powder followed by compaction, (ii) co-precipitation or (iii)
addition in the cement paste of compounds for bone
regeneration. With regard to the stimulation of bone regenera-
tion specific proteins have been administrated via calcium
phosphate carriers. Bone morphogenetic proteins (BMP,
especially BMP-2) adsorbed onto ceramics [267,268] or co-
precipitated with carbonated apatite coatings [91] induce more
bone formation than ceramics alone in vivo. Recently,
incorporation of silicate and zinc ions, respectively in
tricalcium phosphate and hydroxyapatite ceramics, were
reported to have a significant influence on osteogenesis in
vitro and in vivo [260–271]. However, the mechanisms of
release profile versus the nature of the calcium phosphate
remains poorly investigated.
Degradable polymeric biomaterials have been extensively
used for controlled drug delivery systems. The therapeutic
molecular cargo can either be incorporated directly in the
biomaterial matrix, or added to a prefabricated biomaterial by
mean of microspheres [272–274] or coatings [275]. PLA, PGA,
PLGA have already been studied for drug delivery [272,276–
282]. The release rate of incorporated proteins is linked to the
degradation rate of the polymer. However, it is possible for the
activity of the incorporated protein to decrease, due to its
denaturing in view the degradation mechanism of this class of
polymers [283–285]. For long term release, another linear
aliphatic polyester commonly used in tissue engineering is
poly(e-caprolactone) (PCL) is attractive as its degradation rate
is slow compared to other common biocompatible polymers
[174,256,286,287]. PEGT/PBT biomaterials allow the embed-
ding of proteins in their matrix [92]. The release mechanism is
due to a combination of protein diffusion and matrix
degradation, which allows zero-order release profiles over
long time period. A further modulation in degradation rate and
protein release profile can be achieved by substituting part or all
of the terephthalate groups with succinate blocks during the
copolymerization reaction [288–290].
In gels, bioactive agents can be easily incorporated [74,291].
However the bioactivity of these agents may be hampered when
they are combined with in situ polymerizable hydrogels due to
the exposure to ultraviolet light and crosslinking agents which
can induce protein denaturing or aggregation, and decrease the
activity of encapsulated proteins [292]. Natural polymers jellify
chemically, they can readily serve as drug delivery systems. For
example, collagen and polysaccharide matrices allow the
release of proteins and growth factors by diffusion, degradation
of the matrix [293–303,16,304].
In general, the incorporation of bioactive agents in
polymeric biomaterials can be achieved by dispersing the
protein in the polymer phase prior to scaffold processing, using
two main approaches: (i) adding the signaling molecule directly
to the polymer solution or powder [281] or (ii) a water phase
containing the protein can be mixed with a polymer dissolved in
an organic solvent to form a water-in-oil (w/o) emulsion
[273,276]. However, this may induce a loss of activity due to
protein denaturing [285]. The association of growth factors to
porous biomaterials is usually achieved by separating the
scaffold preparation step from the protein incorporation, to
reduce the detrimental effect of scaffold processing on protein.
Growth factor loaded microspheres or liposomes were
incorporated in hydrogels or prefabricated scaffolds
[168,301,305], polymer coating applied on compression
molding scaffolds [275] or, more often, prefabricated matrices
were soaked with growth factor solutions [304,306,307].
Although adsorption of the growth factors by soaking seems the
easiest and less harmful approach, it limits the possibility to
control the release of growth factors from the scaffolds. In
addition, it was demonstrated that adsorption could also result
in protein denaturing [308].
Studies have confirmed the potential of local controlled drug
delivery systems for tissue repair and regeneration. In vitro, the
sustained delivery of two growth factors, TGF-b1 and IGF-1,
supported cartilage repair and maintenance [274,300,301,305].
In vivo, the beneficial effect of growth factors sustained release
was as well demonstrated. In rabbit osteochondral defects, the
release of TGF-b1 over at least 5 days from alginate
microparticles [298] or a release of BMP-2 within 10 days
from collagen sponges were evaluated [309,310]. An improve-
ment of the tissue repair after 6, 12 or 24 weeks was measured,
in comparison to defects filled with unloaded matrix or left
empty. BMP-2 delivery showed similar cartilage restoration as
compared to the implantation of autologous chondrocytes in the
defect. This indicates the potency of the released growth factors
to differentiate progenitor cells present at the implant site,
which may eliminate the need of an extra cell source for
transplantation. However, recent studies in rabbit osteochondral
defects with scaffolds releasing TGF-b1 at similar concentra-
tions showed either only a limited improvement of cartilage
restoration [311] or no improvement when released over 12
days [312]. The same negative result was found in chondral
defects exposed to IGF-1-releasing liposomes, possibly
because of a wrong dosage or release rate which was not
evaluated, or to the lack of suitable progenitor cells [167].
Thorough systematic studies have shown the biological
sensitivity to degradation and drug release kinetics. However,
controlled and well-defined delivery systems to regenerate
tissues still have to be proven in clinics as tissue growth varies
between individuals, species and location of the tissues.
5.3. The role of proteins in regulating biomaterial-induced
biological response
Several properties have been proposed as potential
regulators of cell behavior including wettability (as measured
by water contact angle), surface chemistry, equilibrium water
content, surface flexibility and roughness [313–315]. However,
it is likely that a combination of these factors collectively
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7156
influences cell function, possibly by modulating the adsorption
of proteins onto attachment substrates. Although the natural
state of most proteins is in an aqueous environment, the contact
of a protein solution and a solid phase with which it is
immiscible leads to the accumulation of the protein between the
two phases [316]. The physicochemical properties of the
protein and chemistry of the solid phase would then determine
whether the protein adsorbs to the substrate. This is the scenario
when seeding and culturing cells on biomaterials in serum-
containing media conditions. Thus, in addition to direct cell–
material interaction, it is plausible that cells would also sense
the biochemical environment of the adsorbed proteins and that
this substrate-protein environment could markedly influence
cell behavior [317].
5.3.1. Protein adsorption onto biomaterials
Mammalian cells have long been cultivated on organic
polymers substrates for basic cell research [318–320] and the
advent of cell therapy and tissue engineering have reinforced
the need to understand cell–biomaterial substrate interactions
[3,48,123]. Among the techniques used to modulate protein
adsorption is the inclusion of specific molecules such as PEG
polymer chains at the surface of biomaterials. Incorporating
PEG increases hydrophilicity and mobility of surface
molecules [321,322]. It is achieved by grafting PEG to
hydrophobic surfaces, simple PEG adsorption or by synthesiz-
ing block copolymers containing PEG components [323].
When exposed to water, PEG chains become highly mobile to
form a large excluded volume in a liquid-like state [324]. PEG
length correlates directly with the volume of protein adsorp-
tion-inhibiting mobile water molecules present at the surface
[324].
The primary serum proteins believed to be involved in cell
attachment and growth on polymer substrates are fibronectin
(Fn) and vitronectin (Vn) and several reports have shown that
Vn, rather than Fn, preferentially adsorbs to some substrates
from serum [325–327]. It was also previously reported that Vn
adsorption was not inhibited by increasing PEG concentration
at a surface, regardless of substrate wettability [325] and that
Vn adsorbed equally well to untreated polystyrene (PS) as it did
to surface modified tissue culture polystyrene (TCPS) [328].
The presence of serum proteins has been demonstrated to be
more effective in inhibiting Fn adsorption to bacteriological
grade PS, as compared to TCPS [329]. Since the adsorption of
Fn to substrates has been shown to correlate with cell
attachment, this suggests that glow discharge treatment of
surfaces enhances cell adhesion by allowing increased Fn
adsorption from serum. However, TCPS is more hydrophilic
than bacteriological grade PS because treatment with glow
discharge increases wettability, which appears counter-intuitive
since it is also generally accepted that wettability and cell
adhesion are inversely related. However, this treatment also
forms charged oxygen-based functional groups at the surface
[320,330,331]. The charges endowed by these chemical groups
may dominate wettability, with respect to protein and cellular
interactions, and may be the reason for the difficulty in
correlating wettability and cell attachment over a wide range of
substrates [313,332–334]. However, the relationship between
Fn adsorption and cell attachment suggests a synergistic
relationship between Fn adsorption and chemical charges with
respect to cell adhesion [329].
At the surface of calcium phosphate ceramics, proteins
interfere with the ionic exchange mechanisms as observed in
vitro for calcium phosphate ceramics. These interactions
depend on the bioceramics’ characteristics (e.g. phase,
crystallinity, composition and texture) [335–337] and on the
properties of the proteins (e.g. conformation, isoelectric point),
concentration and whether they act in solution or on substrates
[193,338–341]. First, in suspension, proteins can inhibit or
support calcium phosphate nucleation and growth
[193,338,342]. Regarding bone proteins such as collagen,
osteopontin, osteonectin, bone sialoprotein or osteocalcin,
phosphorylated entities have demonstrated their ability to
nucleate and grow calcium phosphate crystals [342]. However,
not all of the phosphorylated proteins induce calcium phosphate
formation; osteopontin is a particularly strong crystallization
inhibitor [338]. Second, when proteins adsorb onto calcium
phosphate substrates, their charge, concentration and the
presence of calcium in the surrounding fluids influence the
surface coverage kinetics and pattern that can evolve with time
[343]. These adsorbed proteins can thereafter influence the new
formation of calcium phosphate crystals by blocking the
substrate’s nucleation sites [339–341], irrespective to the
protein’s isoelectric point [340]. In vivo, hundreds of proteins
are present in biological fluids and their global effect on
calcium phosphate reactivity is insufficiently understood. An in
vitro study conducted on a large panel of serum proteins
adsorbing on different inorganic materials, including calcium
phosphate ceramics did not show significant differences despite
the physical and chemical characteristics of these materials
[344]. It is clear however, that they play a significant role in
ionic exchanges and their subsequent effect on their biological
activity, since proteins are detected in close association with the
nanocrystalline carbonated apatite formed on the surface of
calcium phosphate bioceramics in vitro and in vivo
[190,192,193,196,204,345]. Consequently, the nature, quantity
and conformation of these proteins at the biomaterial surface
will determine cellular activity [335,337]. The specific pattern
of protein adsorption has been hypothesized as an influencing
factor in the osteoinductive properties of biomaterials.
5.3.2. Smart designs to control protein adsorption
The ability of materials to modulate downstream gene
response without exogenous growth factors, coatings or
complex ligand incorporation has the potential to greatly
facilitate the development of tissue engineering and cellular
therapies. As an illustration of this concept, a class of biphasic
calcium phosphate ceramic induced de novo bone formation at
non-osseous sites in vivo without requiring the delivery of cells
or biologic compounds [9], suggesting that the surface
chemistry of the ceramic allowed the selective adsorption of
morphogenetic proteins that trigger osteogenesis. It was also
demonstrated using polymer libraries that substrate chemistry
can influence the developmental lineages of embryonic stem
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 57
cells [7]. We have reported data that demonstrated that
chondrocytes cultivated on PEGT/PBT substrates can be
induced to express highly specific cell behavior, including
modulation of phenotype. This was evident at the cell-surface
receptor, focal adhesion complex, cytoskeletal, intracellular
signaling and gene expression levels, illustrating the versatility
of smart materials in designing the material–biologic interface
[346]. It was found the profiles of adsorbed proteins at the
material surface played a key role in the downstream cellular
response. In principle, this ability to ‘dial in’ the required
biological response from the substrate allows us to establish cell
function and fate by eliciting the interfacial conditions that
regulate signaling to and from the transplanted cells.
Molecular imprinting is also a sophisticated technique to
tether specific biological entities at biomaterial surfaces. This
strategy consists of constructing ligand selective recognition
sites onto synthetic materials where a template (atom, ion,
molecule, complex, molecular, ionic or macromolecular
assembly, including micro-organism) is employed in order to
recognize site formation during the covalent assembly of the
bulk phase by a polymerization or polycondensation process,
with subsequent removal of some or all template being
necessary for recognition to occur in the spaces vacated by the
templating species [347]. This technique is applied in
chromatography, membrane separations, solid phase extrac-
tion, immunoassays, synthesis, catalysis and sensors. Recently,
Alexander et al. reviewed the current therapeutic molecular
imprinting applications, imprinted materials have attracted
attention as vehicles for controlled release of drug, and as
screening tool in drug discovery. The use of molecular
imprinted sensors has enabled the thorough screening of
combinatorial libraries, and the synthesis of drug candidates in
the recognition sites of imprinted materials [347]. With regard
to tissue regeneration, imprinting sites onto a biomaterial in
order to attract molecules favorable to tissue formation could be
a smart way to instruct the body to heal by itself, avoiding
therefore exogenous entities.
5.4. Controlling cell–biomaterial interactions
In general cells/biomaterial interactions depend on the
surface characteristics such as topography, chemistry and
surface physics. As mentioned earlier, surface characteristics
determine ionic exchange dynamics and protein adsorption.
They also affect cellular activity, namely, cell attachment,
proliferation and differentiation.
5.4.1. Cellular activities and functions on biomaterials
In contrast with differentiated osteoblasts and chondrocytes,
mesenchymal stem cells are migratory, highly proliferative
cells and have greater differentiation potential. They can
migrate on a substrate by generating cycles of weak adhesion,
traction, movement and detachment. At the end of the
migration phase, mesenchymal/osteoprogenitor cells adhere
onto the substrate by developing strong focal adhesion with
substrates in order to start their differentiation phase, similar to
osteoblasts or chondrocytes. Cell migration and adhesion are
mediated via integrins which are transmembrane proteins
[348]. Fibronectin and vitronectin are serum proteins that are
ligands for integrins, and have been shown to mediate adhesion
to biomaterials in vitro [337,348]. In contact with the
biomaterial, the attached cells may further differentiate and
produce specific extracellular matrix components (see Fig. 5 for
a general overview of the mechanistic events that occur during
this process).
It has been shown that chondrocyte attachment and
spreading on two-dimensional surfaces leads to the loss of
expression of aggrecan and type II collagen, a phenomenon
known as ‘dedifferentiation’ [349–353]. Though not strictly a
movement along the cell’s differentiation lineage pathway to
yield a more primitive progenitor cell, it refers to
chondrocytes exhibiting fibroblast-like characteristics, such
as cell morphology and non-phenotypic protein expression
and synthesis. The ability of chondrocytes to rapidly alter
their differentiated phenotype and gene expression following
attachment makes them an interesting cell type to study
phenotype modulation by controlled variations in substrate
properties.
5.4.1.1. Cell surface receptors are the link between a cell’s
externally-induced signals and intracellular signaling
pathways. Ligand-receptor signaling is critical in determining
the fate of differentiated chondrocytes and osteoblasts, as well
as progenitor cells of these lineages. This is governed by
substrate/protein interactions with cell surface receptors known
as integrins (integral membrane receptors). Integrins are
heterodimers of transmembrane a and b subunit proteins that
are involved in cell–cell binding as well as cell–substrate
adhesion. Different combinations of a and b subunits are
possible, with the b1 subunit being most promiscuous in its
ability to form dimeric receptor complexes. More than 15 a
subunits and 8 b subunits have been identified with most
integrins also able to bind to multiple ligands at the integrin
headpiece [354].
Of the different integrins tested, chondrocytes in situ have
been shown to most abundantly express a5b1 and the cell
surface expression of this integrin is markedly increased during
in vitro proliferation in monolayer [355]. Other integrins found
at cell surfaces of adult articular chondrocytes include a1b1,
a3b1, avb5 and avb3 [356]. However, fetal chondrocytes
were shown to express a2b1 and a6b1, indicative of the
different roles of integrins during development and homeostasis
[357].
Certain ECM and adhesive proteins such as fibronectin and
vitronectin bind to integrins primarily by Arg-Gly-Asp (RGD)
peptide sequences contained within the proteins’ cell binding
domains. The RGD sequence is able to adopt variable
conformations in different proteins, and this conformational
flexibility has been suggested as a factor in integrin-ligand
specificity [358]. Studies examining the effects of RGD
peptides on chondrocyte behavior has revealed the suppression
of chondrocyte differentiation in the epiphyseal plate and the
inhibition of chondrogenesis in mouse limb bud cells
[359,360]. This demonstrates the importance of integrin-based
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7158
signaling in cartilage development, and is being leveraged by
stem cell and regenerative medicine scientists in decoding the
signals required to stimulate the differentiation of stem
cells towards the chondrogenic or osteogenic lineages
[149,361,362]. Recent reviews have elegantly elaborated on
signal transduction pathways and signal transmission to the
cytoskeleton by ligand binding to integrins [363,364].
In addition, differentiated chondrocytes also express CD44,
a transmembrane proteoglycan receptor that is the principal
receptor involved in binding to hyaluronan [365,366]. It
enables the retention of the hydrated aggrecan aggregates at
chondrocyte surfaces, which can be released from the surface
by the addition of small HA oligosaccharides or CD44
Fig. 5. Cellular events at a biomaterial surface. (a) Colonization and attachment;
antisense nucleotides [141,366]. The extracellular domain of
this receptor contains strong sequence similarities with HA
binding regions in link protein and chondroitin sulfate side
chains [358]. Chondrocyte delivery substrates for tissue
engineering applications that enable cell–substrate binding
via CD44 are able to maintain the differentiated cell
phenotype. The intracellular domain of CD44 associates with
cytoskeletal proteins and can regulate signaling in this manner
by the coordinated activities of actin network modification and
protein phosphorylation, primarily through interaction via
tyrosine kinases, ankyrin and ezrin/radixin/moesin (ERM),
leading to differential states of phenotypic expression
[364,367].
(b) proliferation; (c) migration; and (d) differentiation and tissue formation.
Fig. 5. (Continued ).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 59
5.4.2. Effect of surface physico-chemistry
Chondrocyte function is known to depend on the adsorption
of specific ECM proteins on the culture substrate: it has been
shown that vitronectin is required for chondrocyte adhesion to
methacrylate-based polymer substrates [327] and fibronectin
enhances chondrocyte dedifferentiation in monolayer culture
[368,369]. Although wettability has been shown to influence
biomaterial–cell interactions and is often used as a parameter
by which to characterize and compare biomaterial surfaces
[313,370], conclusive correlations linking wettability, protein
adsorption and cell function have yet to be made [332,333,371–
374]. However, these assays have usually been performed using
a limited range of substrates and do not address material–
protein interaction over a wider range of material properties.
Understanding such interactions is of considerable importance
in cell transplantation therapies since the resulting cell–
material constructs are implanted into the defect site with the
desired goal to mimic the important properties of cartilage,
thereby enabling improved functionality [122]. To elucidate the
effects of selecting certain materials for such cell transplanta-
tion therapies, it is crucial to understand the cell–material
interactions that occur during this process, from cell attachment
to downstream signal transduction events.
In the bone environment, some biomaterials have an
intrinsic ability to bind with newly formed bone with a
physico-chemical continuity. Calcium phosphates and bioac-
tive silica glasses, are the first bioceramics that have been
specifically developed for bone repair. The idea behind the
development of these bioceramics was that making synthetic
materials with composition similar to bone mineral would
improve their biocompatibility and acceptance by host bone.
These bioceramics indeed exhibit excellent bone-bonding
properties that are related to the surface reactivity, via
dissolution–precipitation mechanisms, creating an interfacial
mineralized layer between the implant and bone tissue that
insures their cohesion. Structurally, this layer is comparable to
the films grown in vitro by dissolution–precipitation mechan-
isms, i.e. nanocrystals of carbonated apatite [19,190–194], in
simulated body fluids that mimic the mineral composition of
blood plasma. When formed in the presence of osteogenic cells
experiments, this mineralized layer is comparable to the cement
lines synthesized in vivo [31,195]. In vivo (osseous and non-
osseous environment), physicochemical and crystallographic
continuity are observed between the calcium phosphate implant
and the newly formed mineralized layer [19,196,197]. Its
occurrence and thickness are related to the reactivity
(dissolution–precipitation) of the calcium phosphate substrate
[197], also referred to as ‘bioactivity’ [198]. This mineralized
interface ensures a physicochemical and mechanical cohesion
between the implant and the host bone (Fig. 4a and b). It is
particularly relevant for load-bearing applications, such as hip
metallic prostheses coated with calcium phosphate which layer
improve undoubtedly the mechanical stability of the implant by
augmenting and accelerating the bone apposition [199–201].
The bone-bonding ability of these bioactive biomaterials is also
exploited in bone tissue engineering [202].
Fig. 4 shows bone formation at the surface of metal and
apatitic implant biomaterials.
5.4.3. Effect of topography
Surface roughness is generally known to influence cell
attachment in vitro, including attachment of bone cells. Rough
apatitic surfaces appear to enhance osteoclastic attachment
compared with smooth ones [375]. Grooved surfaces influence
osteoblast guidance, as does the groove profile and topography,
independent of the chemical nature of the substrate [376]. On
the other hand, on micro- and macroporous calcium phosphate
ceramics, osteoblasts sense the surface microporosity and can
bridge even large pores many times larger than fully spread
osteoblasts [377]. With regard to osteoblasts differentiation,
Chou et al. demonstrated in vitro that osteoblastic cells were
sensitive to crystal shape: large apatite crystals induced more
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7160
bone sialoprotein and osteocalcin expression after 3 weeks of
culture [94]. Finally, Redey et al. have shown that surface
energy strongly affected initial osteoblast and osteoclast
activity. In vitro, early osteoblast proliferation and function
and osteoclast adhesion are affected by the polar component of
the calcium phosphate surface. However, at a later culturing
stage, surface energy does influence anymore both osteoblast
and osteoclast activity [378,379]. Thus, adjusting the under-
lying micro- and nanotopography is also a smart way to trigger
and modulate specific cellular functions.
5.4.4. Micro- and nanodesigns of biomaterials
Cell dimensions generally range from 5 to 100 mm.
Regardless their type, cells can react to micrometer and
nanometer scales. The realization that the physical features of
the substratum on which cells are growing can affect their
morphology and migration dates to the 1930s, but it was not
until the development of micro- and nano-fabrication methods
that a wide range of physical features could be made on the
micro- and nanometer scale. Surface topography can affect
various cellular reactions, namely cell orientation, adhesion,
movement, gene expression, activation of phagocytosis and
orientation of the cytoskeleton in vitro [380]. In vitro micro-
features with specific shapes can influence the cellular
activities, including osteogenic differentiation [381]. In vivo,
the surface microtopography can significantly affect tissue
neoformation. For example, the initial surface roughness of the
titanium prostheses greatly influences early bone formation and
contact with the implant [382,383]. More recently, the micro-
texturing of macroporous biomaterials induced bone formation
in non-osseous environment [210], and micro-grooved hollow
fibers induced tendon regeneration [384].
Webster et al. have demonstrated that the presence of
nanophases (smaller than 100 nm) in titanium oxide, alumina
and hydroxyapatite substrate could have consequences on bone
cells activity and functions [385–387]. Independent of ceramic
composition, osteoblasts and osteoclasts favored the introduc-
tion of nanophases into the ceramic [385,386]. Examination of
the underlying mechanism(s) of cell adhesion on nanophase
ceramics revealed that these ceramics adsorbed significantly
greater quantities of vitronectin (an adhesion cellular protein),
which, subsequently, may have contributed to the observed
select enhanced adhesion of osteoblasts. Select enhanced
osteoblast adhesion was independent of surface chemistry and
material phase but was dependent on the surface topography
(specifically on grain and pore size) of nanophase ceramics
[388].
Several techniques, namely electron beam lithography,
colloidal resists, self-assembling systems, casting, micro-
contact printing, masters made by one of the above techniques
and particle synthesis, are nowadays available to create
nanotopography on organic and inorganic surfaces [380]. It
has been demonstrated that cells can react in vitro to objects as
small as 5 nm, which are 1000–5000-fold smaller in size [389].
Curtis et al. have shown a relation between symmetry and
regularities of nano-objects and cellular adhesion. With cliffs,
adhesion is enhanced at the cliff concave edge, while pits or
pillars in ordered arrays diminish adhesion. The results
implicate ordered topography and possibly symmetry effects
in the adhesion of cells. More precisely, the asymmetry and the
presence of concavities may increase the wettability of the
substrate, and therefore enhance cell adhesion [390]. Other
reports on the cellular interactions with specific nano-patterned
substrates of various composition have shown that nano-shaped
holes can also (i) control cell life and death [391] and (ii) orient
cell commitment towards osteogenic lineage [149,392]. The
influence of surface nanotopography on cell behavior is
mediated via changes in the orientation and conformation of
proteins that interact with the nanotextured substrate
[386,393,394].
Micro- and nano-patterning can include modification of
surface chemistry or topography. Nano-patterning can consist
as well at grafting chemical functions onto biomaterials. In the
field of tissue engineering, the grafting of RGD peptides has
been the focus of much attention [395,396]. Their presence at
biomaterials surfaces improved cell adhesion. Indeed this
peptide sequence is present in various extracellular matrix and
plasma proteins, and it constitutes a major recognition site of a
large number of adhesive extracellular matrix, blood and cell
surface proteins [358]. Other peptides and organic molecules
have been used to stimulate cell adhesion [236,397,399]. Zhang
et al. could design adhesive arrays and patterns for cells by
combining two types of oligopeptides on a flat substrate [398].
Other patterned substrates containing two different peptides
could specifically and locally induce the adhesion of two
different cell types relevant in the field of bone tissue
engineering (osteoblasts and fibroblasts) [397]. Small changes
in the graft can induce significant differences in the efficiency
of the cellular adhesion [236,399]. For example, alkylsilanes
were also grafted on model surfaces. The nature of their
termination (epoxide, carboxyl, amine, or methyl) strongly
affected cellular adhesion [236]. The grafting of specific
function does not concern solely cellular interactions, but aims
also at the immobilization of bioactive molecules. Puleo et al.
could immobilize an osteoinductive protein (BMP-4) after
plasma polymerization of allyl amine. Cells cultured on this
BMP-4 immobilized biomaterials differentiate towards osteo-
genic lineage. This indicated that the bioactivity of the BMP-4
was retained trough the immobilization process [400].
However, similar titanium surface treatment favored also the
immobilization of another protein. No evidence was shown that
this immobilization technique was specific to a particular
bioactive molecule.
Although micro-patterning has proven a biological effect in
vitro and in vivo, long term in vivo consequences of nano-
patterning remain to be demonstrated.
5.5. Multi-functional scaffolds
Tissues are multi-component and multi-functional, while
current biomaterials are designed to replace only one
predominant function. The natural tissue repair process
involves multiple signaling molecules, in a time and
concentration-dependent fashion, as is clearly established for
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 61
bone repair [401–403]. In bone tissue engineering, the main
focus has been on bone forming biomaterials and bone forming
cells. However, the poor viability of newly formed tissues has
underlined the need for their early vascularization [404]. The
design of biomaterials and cell systems is focusing increasingly
on the simultaneous development of bone tissue and vascular
network. Trauma and joint diseases frequently involve both the
articular cartilage surface and underlying subchondral bone.
Making a mechanically stable construct, that can bear the
articular loads and would support both bone and cartilage
formation, is an important goal in tissue engineering.
5.5.1. Multiple-component scaffolds
A more recent strategy consists of combining biomaterials
with intrinsic properties that stimulate the formation of specific
tissues into a multi-phasic construct. For example, a poly-L-
lactic acid/hydroxyapatite composite was produced after
image-based design and solid-free form fabrication with the
aim to generate a biomaterial matching the load-bearing and
articular geometry [405,406]. In vivo, the chondral zone seeded
with chondrocytes and the osseous zone loaded with BMP-7
transfected fibroblasts showed the formation of cartilage and
bone, respectively [405]. A more clinically relevant approach
consists of using one cell source, such as mesenchymal stem
cells, that differentiate into cartilage and bone in well-defined
sites. Towards this end, triphasic scaffolds have also been
fabricated for osteochondral defects using an osteoinductive
Fig. 6. Examples of multi-functional scaffolds designed based on 3D-fibres deposit
with osteoinductive BCP inserts (a), the cartilage and bone compartments are tight
polymeric scaffold: (c) the fibres are composed of two different polymers (outer an
calcium phosphate ceramic in combination with a copolymer
composed of poly(ethylene glycol) (PEGT) and terephthalate-
co-poly(butylene terephthalate) (PBT), with different mole-
cular weight of the starting PEG blocks, and different weight
ratios of the PEOT and PBT blocks. The copolymer was
selected among others as it has shown better results in terms of
mechanical properties for cartilage repair applications, and cell
attachment for bone tissue engineering [407,408]. The porous
triphasic structure has been obtained by three-dimensional fiber
deposition technique, with mechanical integrity achieved by the
deposition of layers of circular and concentric fibres of the two
polymer compositions (Fig. 6a). Another example of a multi-
functional scaffold consists of embedding hollow fibres within
a bulk scaffold in order to favor the formation of neo-
vasculature within the scaffold that would integrate with the
native host vascular network. In a representative study, Moroni
et al. demonstrated the encapsulation of fibers within a scaffold,
exploiting the differential melting temperatures and viscosities
of two polymers, as shown in Fig. 6b [275].
5.5.2. Multidrug delivery
This technique consists of the smart combination of signals
able to stimiulate in parallel several cell types and tissues. This
approach can be obtained by multi-drug delivery systems or by
employing multiple scaffold components.
Multi-drug delivery attempts have been made using
biomaterials in the shape of rods [409], hydrogels [305], or
ion. (a, b) triphasic osteochondral construct combining two polymeric scaffolds
ly glued together with a mixture of the two polymers (b); (c, d) hollow-fibres
d inner shell), and (d) after dissolution of the inner shell (courtesy L. Moroni).
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7162
gelatin layers [410]. Porous scaffolds as reservoirs for multiple
proteins were obtained by assembly and fusion with micro-
spheres [278,279] or by associating them with pre-existing
porous structures [300]. Regariding cartilage repair, the
opportunity to combine the release of different growth factors
was investigated by mixing IGF-1 and TGF-b1-containing
PLGA microspheres in a hydrogel [305]. This approach
appeared promising as the two growth factors had synergistic
effects on the enhancement of chondrocyte proliferation and
maintenance of their phenotype. In a broader view, it is likely
that the release from scaffolds of different growth factors with
different release profiles would be therapeutically beneficial.
Other methods have also been considered for this purpose. For
example, mixing two populations of gelatin microparticles
releasing IGF-1 and TGF-b1 within an hydrogel or adsorbing
TGF-b1 to the hydrogel directly, allowed independent control
of the release profiles of the two proteins [411]. Another
approach consists of applying multiple gelatin coatings
containing BMP-2 and IGF-1 on flat surfaces to control the
release of each growth factor independently by diffusion
through the superposed layers [410,412]. Similarly, the
successive coating of PEGT/PBT copolymers containing
different model proteins on prefabricated compression-molded
scaffolds allowed a tailored and independent release [274].
However these techniques are yet preliminary and still have to
be tested in relevant articular cartilage defect models in vivo.
The incorporation of different signaling molecules has also
been studied in order to induce simultaneous bone formation
and neo-vascularization. The bi-functionalization of (poly-
lactic-co-glycolic-acid) porous scaffolds was achieved by two
different protocols and investigated in vivo. In one experi-
mental group, an angiogenic factor (vascular endothelial
growth factor, VEGF) and an osteogenic factor (plasmid-
DNA encoding for BMP-4) were aggregated at the scaffold
surface [413]. These bi-functional scaffolds associated with
mesenchymal stem cells in vivo, and showed significant
increase in bone regeneration and blood vessel formation. In
another group, a calcium phosphate layer was combined with
VEGF containing porous scaffold before implantation. The
presence of both VEGF and calcium phosphate layer in a single
scaffold induced more blood vessel formation than either
component alone. However, bone tissue formation was not
significantly higher than the mono-functionalized scaffolds
[282]. In both studies, it was not clear whether a connection was
established between the engineered vascular system and the
host vasculature. The perfusion of the engineered vascular
network is essential for the viability of the tissue engineered
construct, as it was shown in a model system for muscle tissue
engineering [414]. Truly smart systems will connect the
vasculature between the implant and host tissue.
5.6. Three-dimensional control of biomaterials on cells
and tissues
In tissue regeneration, the three-dimensional features of the
biomaterial are of high relevance as it affects the activity of
various cell types, the subsequent tissue neoformation and
viability. Spatial effects of biomaterials are evident in vivo from
the centimeter to nanometer scales. For example, the angle of
curvature of a hip stem can significantly affect the prosthesis
integration. Biomaterials, used to fill tissue defects, act as an
exchange platform between the hosting tissues and the implant.
Their three-dimensional organization and features will play a
critical role in these exchanges, namely, (i) the selective
penetration of cells, nutrients and oxygen, and tissues, (ii)
clearance of metabolic products, (iii) proliferation and
differentiation of cells, (iv) neo-formation and viability of
desired tissues, and (v) degradation of the biomaterial. The
biomaterials options supporting these exchanges are either
porous solids or hydrogels.
With respect to bone biomaterials, porous solid structures
are preferred because osteogenic differentiation is positively
influenced by strong adhesion onto surfaces [174]. In osseous
environments, scaffolds having higher porosity (percentage of
void space in a solid) and pore size stimulate greater bone
ingrowth. However, this trend results in diminished mechanical
properties, thereby defining a practical upper limit for pore size
and porosity. A recent review established that the minimum
requirement for pore size is considered to be approximately
100 mm due to cell size, migration requirements and nutrient
transport. However, pore sizes >300 mm are recommended, to
achieve enhanced new bone formation and the formation of
blood capillaries. The vascularization of the porous biomaterial
is desired as early as possible, as it allows a constant and local
delivery of oxygen and nutrients during tissue morphogenesis.
This efficient transport of oxygen and nutrient are necessary for
both transplanted cells and newly formed bone survival inside
the scaffold. Interestingly, small pores favor hypoxic conditions
(low oxygen concentration) and induced cartilage formation
before bone [415]. Therefore, regardless of biomaterial
composition, it is possible to direct either bone or cartilage
formation via the control of the pore size. In principle, by
preparing a gradient in pore size, one could simultaneously
stimulate bone and cartilage formation at desired locations in a
single scaffold.
In addition to the porosity and pore size, the shape of the
pores can also play a pivotal role. We reported earlier, that, for a
given biomaterial, only macropores with specific geometry can
induce bone formation in non-osseous sites [197,226]. Pore
confinement has been also pointed out as a critical factor [88].
In addition, the size of the macroporous implant influences as
well its osteoinductive abilities. In goat muscles, Habibovic
et al. observed that the larger the implant, the more bone
formation is induced [219]. The three-dimensional character-
istics of the biomaterials clearly have marked effects on cell
behavior, and therefore on tissue formation. However, the
complete picture of processes involved in biomaterial regula-
tion of biological mechanisms remains unclear.
To date, unorganized porosity seems to play a positive role in
tissues. It is a challenge to ascertain exactly which parameters
play dominating roles in instructing the biological response,
improved understanding of which would help in designing
better biomaterials. Designing, controlling and characterizing
porous structures from the macro- down to the nanometer scale
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 63
still demand tremendous technical improvements in multiple
areas.
Polymer hydrogels have also been designed for responsive-
ness to their local biological environment. These can be based
on both synthetic or natural polymers, and have been defined as
hydrophilic polymers that swell by taking up water in the range
of 10% to �103-fold their dry weight [416,417]. In general,
these materials can be classified as either chemical or physical
hydrogels. Chemical hydrogels are crosslinked, with nodes of
high crosslinking density in a mainly low crosslinked structure.
Conversely, physical hydrogels are supported without covalent
interaction, and contain both hydrophilic and hydrophobic
domains. Water uptake occurs sequentially at the hydrophilic,
hydrophobic and interstitial regions to cause swelling.
Hydrogels have been made to be responsive to a number of
stimuli, including: pH, Ca2+, Mg2+, organic solvents, tempera-
ture (including sol–gel transition), external magnetic fields,
electric potential, UV, IR and ultrasound [112,419–431].
Among the frequently studied hydrogel systems is poly(N-
isopropylacrylamide) [432–436]. This family of thermosensi-
tive hydrogels has the ability to collapse above a specific, pre-
defined temperature (lower critical solution temperature—
LCST). Below the LCST, the hydrogel is dehydrated and
hydrophobic, whereas above the LCST, it is hydrated and
hydrophilic. An additional degree of responsiveness can be
attained with the inclusion of methacrylic acid, which makes
the structures responsive to both temperature and pH. Other
combinations include responsiveness to light and temperature,
or Ca2+ and temperature. The potential of such materials is
derived from their ability to transplant cells or locally
administer growth factors based on specific biochemical cues,
ex vivo or in vivo.
5.7. Physical stimuli on cells
It has been known for more than a hundred years that bone and
cartilage are sensitive to mechanical loading: cartilage is able to
remodel only when mechanical load is applied and bone density
patterns are governed by the distribution of stress. Nowadays, we
now that physical stimuli are converted into biochemical stimuli
that affect cellular functions and activities. This conversion can
be divided in four steps: (1) mechanocoupling is the conversion
of the applied physical force to secondary forces or physical
phenomena detected by the cells; (2) mechanotransduction is the
conversion of either the primary or secondary physical stimulus
into an electrical, chemical or biochemical response; (3) the
signal transduction entails the conversion of one biochemical
signal to another; and (4) final step completes the conversion
from initial stimulus to final tissue-level response. The four steps
outlined above suggest methods by which the mechanical or
biochemical environment may be modified to control the
development of engineered tissue. For instance, one might expect
tissue-engineered bone to increase its density when subjected to
mechanical conditions resembling those known to stimulate net
bone formation in vivo [252].
In vivo, mechanical forces arise from diverse sources such as
muscular contraction resulting in stress and strain of muscle
and tendon, and locomotion generating small amplitude cyclic
compression of bone and cartilage. Blood flow exerts shear
stress on the endothelium, and pressure and cyclic strain is
experienced by the endothelium and vessel wall. Interstitial
fluid flow applies shear stress to bone cells and growth which
stresses skin [252]. These naturally occurring mechanical
stimuli have been mimicked in vitro in order to investigate their
effect on cells [437–439]. It has been reported that the
production of shear stress on rat calvarial osteoblasts cultured
on a collagen scaffold increased the production of osteogenic
markers. In other words, mechanical stimulation stimulated
osteogenic differentiation [438]. Conversely, a pulsatile flow
induced osteogenic differentiation of similar cells [439]. Under
cyclic pressures, cellular functions can be positively or
negatively affected depending on the frequency and duration
of the cycles. Differential effects were reported for osteoblasts,
endothelial cells and fibroblasts [437].
Other types of ‘‘artificial’’ physical stimuli on cellular
behavior have been considered as tools to contribute to tissue
repair and healing [307,440–454], namely electrical
[441,447,451,452] or magnetic field [307,445,454], laser
irradiation [440,449,450], heat shock [449] and ultrasound
[449]. These physical stimuli have been proven to influence cell
activity in vitro, and tissue formation in vivo [257,450,452].
Some of these physical stimuli are applied in clinics to treat
tissue defects [441,449]. Pulsating electrical fields, consisting
at applying a voltage inducing a magnetic field, have been
widely documented in vitro and in vivo for hard and soft tissue
repair [441,448,453,455–457]. The cellular responses, namely
proliferation, differentiation, orientation, depend on the
pulsatile frequencies, total energy of the applied field, and
the maturation stage of the cells [447,449,457,458]. Although
the stimulation mechanisms of these biophysical factors are not
well understood, they influence the cellular production of
proteins [447,453,456,457], growth factors [459], minerals
[460] and free radicals [461]. These pulsating electrical fields
have also been proposed as a therapy against osteoporosis by
influencing osteoclast activity [455,456].
These physical stimuli have been also investigated as factors
contributing to tissue healing after biomaterial implantation,
cell proliferation in vitro [440,451,462,445,463], and in vivo
[257,464]. In vivo, these physical stimuli can, in particular,
affect the orientation of the newly formed and growing tissues
[445], as well as their mechanical resistance to load [464].
Developing biomaterials able to generate physical stimuli
can be of great interests for cellular and tissue stimulations.
Piezoelectric materials are able to generate transient surface
charges under minute mechanical strain. Biocompatible
piezoelectric ceramics and polymers have been developed
for various tissue repair purposes [465–468]. The piezoelectric
barium titanate was investigated as a bone tissue growth
enhancer in the 1980s and 1990s [466,467]. The piezoelectric
features of barium titanate can be detected up to 86 days after
implantation in femurs [467]. The same investigators did not
find any significant difference the polarized and the electrically
neutral barium titanate-tissue interfaces [466]. However, in
another study, Feng et al. reported that the implantation of
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–7164
polarized hydroxyapatite-barium titanate ceramics in canine
jaws promoted the growth and repair of the bone significantly
compared with hydroxyapatite. The growth of newly formed
tissue around the piezoelectric ceramic was found to be
direction-dependent [465]. With regard to nerve regeneration,
piezoelectric polymers, such as polyvinylidene fluoride
(PVDF) have also shown a beneficial effect on nerve cells in
vitro [468]. Within 98 h, polarized PVDF substrates exhibited
significantly greater levels of process outgrowth and neurite
lengths at all time periods compared with non-polarized
substrates. The polarization of PVDF did not induce its physic-
chemistry. Therefore, the stimulating effect on cells could
solely be attributed to the piezoelectric stimulus [468]. The
main drawback of piezoelectric material remains the mechan-
ical deformation required to generate charges.
On the contrary, electrically conductive materials have the
advantage of a non-invasive (external) control over the level
and duration of stimulation [469]. Of the electric conducting
polymers, oxidized polypyrolle (PP) has been the most
thoroughly investigated for use in biological systems
[470,471]. In vivo, nerve cells cultured on PP films and
subjected to an electrical stimulus through the film showed a
significant increase in neurite lengths compared with ones that
were not subjected to electrical stimulation through the film and
tissue culture polystyrene controls [470]. Modified PP has been
more recently developed with the purpose to improve the
degradation properties of the conducting polymers [472].
Another approach to produce conducting biomaterials consists
of blending polylactic acid and carbon nanotubes. When
osteoblasts cultured on the surfaces of these nanocomposites
were exposed to electric stimulation for various periods of time,
there was an increase in cell proliferation and differentiation.
These results provide evidence that electrical stimulation
Fig. 7. The convergence of a multitude of technologies and scientific disciplines h
regeneration.
delivered through current-conducting biomaterials promotes
osteoblast functions that are responsible for the chemical
composition of the organic and inorganic phases of bone [473].
The positive effect of physical stimuli in vitro is clear and
promising, and has been shown in vivo.
6. Concluding remarks
Scientists working in the tissue regeneration field are faced
with complex biological systems. From a biological point of
view, significant improvements have been realized with regards
to investigative research tools, and in our understanding of the
mechanisms involved in tissue and organ regeneration. In
parallel, the materials design and fabrication capabilities and
processing technologies have become increasingly sophisti-
cated. These recent developments are mainly due to the fusion
of several fields (Fig. 7). A challenge that has emerged as a
result of these synergistic combinations is the exponential
increase of possibilities that have to be tested and validated.
Smart paths have to be taken to evaluate all of these smart
materials. High-throughput screening technologies can now be
combined with biological and polymer systems for rapid
evaluation of cellular effects caused by underlying polymer
substrates. For example, Anderson et al. have demonstrated the
ability to screen 3500 polymer compositions for their biological
effects on chondrocytes and neural cells, as well as 1700
compositions for their biological control effects on human
embryonic stem cells [7,249]. As technological advancement
continues in high throughput screening, these tools will enable
rapid assessment of interactions between biomaterials and cells
at the cellular, protein and gene levels, offering new windows
into the regulatory signals transmitted by polymers to the
biological environment. In vivo, ‘‘smart’’ screening models and
as enabled the advancement of novel smart and instructive strategies for tissue
F. Barrere et al. / Materials Science and Engineering R 59 (2008) 38–71 65
biomarkers have been developed to better select biomaterials
from a plethora of options [474]. The acquisition of all of the
subsequent biological data will require smart software and data
processing technologies. Closer to mimicking the complexity
of natural tissues, ‘‘smart’’ solutions to regenerate damaged
tissues have emerged, and will further evolve due to the
continued convergence of various fields of expertise.
Acknowledgements
Much of the work presented here is based on the valuable
contribution of the many researchers at the University of
Twente, Department of Tissue Regeneration, including Pamela
Habibovic, Clayton Wilson, Tim Woodfield, Jos Malda,
Shihong Li, Du Chang, Joost de Wijn, Jerome Sohier, Lorenzo
Moroni and Marcel Karperien.
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