SILVER-CONTAINING, SOL-GEL DERIVED BIOGLASS COMPOSITIONS

Abstract: Silver-containing, sol-gel derived bioactive glass compositions and methods of preparation and use thereof are disclosed. The compositions can be in the form of particles, fibers and/or coatings, among other possible forms, and can be used, for example, for treating wounds, improving the success of skin grafts, reducing the inflammatory response and providing anti-bacterial treatments to a patient in need thereof. Anti-bacterial properties can be imparted to implanted materials, such as prosthetic implants, sutures, stents, screws, plates, tubes, and the like, by incorporating the compositions into or onto the implanted materials. The compositions can also be used to prepare devices used for <i>in vitro</i> and <i>ex vivo</i> cell culture.

Description: SILVER-CONTAINING, SOL-GEL DERIVED BIOGLASS COMPOSITIONS FIELD OF THE INVENTION The present invention relates to silver-containing sol-gel bioglass compositions and methods of preparation and use thereof, for example, in preparing biodegradable sutures, bone graft substitutes, matrices for use in tissue engineering applications. This application claims priority to U.S.S.N. 60/139,014, filed June 14, 1999, the contents of which are hereby incorporated by reference. BACKGROUND OF THE INVENTION Materials used for implantation m the human body to replace damaged or diseased tissue must be biocompatible and mechanically suitable for their intended use. Metallic and polymeric materials for biomedical applications present many problems due to their high Young's modulus (compared with that of bone), the formation of a non-adherent fibrous capsule (the resulting movement of which can lead to deterioration in function of the implant), or sometimes to their degradation products. There is an increasing clinical use of bioactive glass and glass-ceramics because they offer the possibility of improving the long-term survivability of prostheses and improved repair of aged, diseased or damaged bone. These materials tend to form mechanically strong bonds to bone by means of a series of chemical reactions at the bone-implant interface. One of the major advantages of using a bioactive glass is the ability to control the surface chemistry, and in doing so, exerting control over the rate of bonding to the tissue. Many biocompatible and bioactive biomateπals have been implanted. Associated problems of infections due to the intrinsic nature of an illness and to surgical intervention can arise as a consequence of implantation, even with currently aseptic surgical procedures. Bioglass ® is one example of a biocompatible material used to prepare implants. Bioglass ® is often used to repair damage caused in bones, teeth, and skm where the potential for bacterial or mycotic infections is always present. An important example is osteomyelitis, one of the most dangerous diseases which is caused, m the majority of cases, by S aureus, Salmonella or K kingea (m children). Even in cases of non-infectious diseases, post-operative conditions often require antibiotic treatment, which is usually administered orally. Unfortunately, this can cause bacteriological resistance to the drug, and often depletes the benign microbial flora normally present in the body, leading to gastrointestinal side effects. Recent efforts have been focused on developing modified implant materials with antibacterial properties. Such implant materials must have suitable mechanical and chemical properties for their intended use. It would be advantageous to provide additional implant materials with antibacterial properties The present invention provides such materials. SUMMARY OF THE INVENTION Silver-containing sol-gel derived bioactive glass compositions and methods of preparation and use thereof are disclosed. The compositions can be in the form of fibers, which can have any diameter between lμ and 150 μm and can be either continuous or discontinuous or particles which can have any diameter for example, from 0.5 μm to 3 mm, or coatings which can have thicknesses, for example, from 0 05 to 100 μm. The bioactive glass (bioglass) used in the compositions includes various salts in the following ranges (weight percent of the bioglass composition): Sι0 2 40-90% CaO 6-50% P 2 0 5 0-12% Ag 2 0 0 1-12% The fibers can be woven into mats and used to make structures useful, for example as bone graft substitutes and coverings for bony defects. The fibers can also be used to make three dimensional structures for preforms to be impregnated with polymers, for example biodegradable polymers. Such structures can be linked, covalently or lomcally, to bioactive compounds, for example growth factors, antibiotics, antivirals, nutrients and the like, to enhance tissue repair and promote healing. The compositions, preferably m the form of fibers or particles, can be incorporated into implanted materials such as prosthetic implants, sutures, stents, screws, plates, tubes, and the like. The compositions in the form of particles can be applied as bioactive layers on prosthetic implants. The compositions m the form of bioactive sol-gel coatings can be applied on the surface or in the pores of prosthetic implants of various configurations. The compositions are also useful for tissue engineering applications. An advantage of using these compositions is that anti-bactenal properties can also be imparted to devices used for in vitro and ex vivo cell culture when the compositions are incorporated into tissue engineering devices. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Silver-containing sol-gel derived bioactive glass compositions and methods of preparation and use thereof are disclosed. The compositions can be in the form of fibers, which can have any diameter between lμ and 150 μm and can be either continuous or discontinuous, particles which can have any diameter, for example from 0.5 μm to 3 mm, or coatings which can have thicknesses, for example from 0.05 to 100 μm. The compositions are prepared using a sol-gel method and can be used for a variety of medical uses, for example bone repair, biodegradable sutures, and tissue engineering applications I. Composition As used herein the terms "bioactive glass" or "biologically active glass" mean an inorganic glass material having an oxide of silicon as its major component and which is capable of bonding with growing tissue when reacted with physiological fluids. Bioactive glasses are well known to those skilled in the art, and are disclosed, for example, in An Introduction to Bioceramics. L Hench and J. Wilson, eds World Scientific, New Jersey (1993), the contents of which are hereby incorporated by reference. The glass preferably includes between 40 and 90% by weight of silicon dioxide (Sι0 2 ), between about 6 and 50% by weight calcium oxide (CaO), between about 0 and 12% by weight phosphorus oxide (P 2 0 5 ) and between about 0.1 and 12% by weight silver oxide (Ag 2 0) . More preferably, the glass includes between 45 and 86% by weight of silicon dioxide oxide (Sι0 2 ), between about 10 and 36% by weight calcium oxide (CaO), between about 3 and 12% by weight phosphorus oxide (P 2 0 5 ) and between about 3 and 12% by weight silver oxide (Ag 2 0). CaF 2 , B 2 0 3 , A1 2 0 3 , MgO and K 2 0, Na 2 0 may be included in the composition in addition to silicon, sodium, phosphorus and calcium oxides. Other silver salts than silver oxide can optionally be used. The preferred range for B 2 0 3 is between 0 and 10% by weight. The preferred range for K 2 0 is between 0 and 8% by weight. The preferred range for Na 2 0 is between 0 and 20% by weight. The preferred range for MgO is between 0 and 5% by weight. The preferred range for A1 2 0 3 is between 0 and 3% by weight. It is preferred to use reagent grade glass, especially since the glass is used to prepare materials which ultimately may be administered to a patient. In a preferred embodiment, the silver-containing, sol-gel derived bioactive glass is formed from various salts in the following ranges (weight percent of the bioglass composition): Sι0 2 45-86% CaO 10-36% P 2 0 5 3-12% Ag 2 0 3-12% Examples of preferred sol-gel derived bioactive glasses are shown below in Table 1, any of which can be modified to include an effective, anti-bactenal amount of silver ions using the methods described herein. Table 1 - Composition (mol. %) of bioactive gel-glasses. Higher CaO contents provide larger pore volumes and the onset of hydroxycarbonate apatite (HCA) deposition is accelerated. Gel-glasses with higher Sι0 2 contents tend to have larger surface areas and exhibit higher growth rates of formation of an HCA layer. Silver Salts Any suitable silver salt can be used which can be incorporated into the bioactive glasses using a sol-gel method. Silver oxide is a preferred salt. Other suitable salts include silver nitrate, silver acetate, silver bromide and silver chloride. The amount of silver m the compositions is generally in the range of between about 0.1 and 12 percent by weight, preferably between about 3 and 12 percent by weight. The toxicity limit for the mgestion of soluble silver salts is about 1 gram for humans, but it is not generally considered a threat to life, as an accidental exposure to high doses of silver is extremely rare. Indiscriminate use of silver-containing pharmaceutical preparations and devices can lead to toxic reactions such as argyπa The term "effective, antibacterial amount" of silver refers to an amount effective to significantly reduce the amount of bacteria in an area proximate to where the bioactive glass is present. This amount would be expected to vary depending on a variety of factors, including the type of bacteria, the bacterial concentration, the type of media and the intended use. Those of skill m the art can readily determine an appropriate, antibacterial amount of silver to use. The bioactive glass compositions can be adjusted to include a variety of concentrations of silver ions. The antimicrobial action of silver has been verified on a number of gram positive and gram negative bacteria, and fungi, among which are E coh, P aeruginosa, S epidermis, C albicans. The enzymes on which the inactivating influence has been studied include; urocmase, β-galactosidase, phosphomannose-isomerase, and several oxygenases It has been postulated that silver exerts its toxicity at multiple sites, among which are the respiratory chain, the phosphate uptake and storage, and the cell wall synthesis. The overall result of these alterations is a lethal leakage of metabolites from the cell, including phosphate and potassium (K0). The mechanism of action of Ag + is believed to be related to its complexation to membranes, enzymes and other cellular components. The silver ion is strongly chelated by electron donor groups such as amines, hydroxyls, phosphate and thiols The latter are thought to be the most important chelating groups, according to microbiological, biochemical and electrochemical data. The silver ion is believed to interact with protein molecules via exposed cyste e residues. II. Methods for Preparing the Fibers, Particles and Coatings Sol-Gel Method The compositions are prepared using a sol-gel method. When compared with conventional glass production techniques, there are a number of advantages associated with the sol-gel process: lower processing temperatures, purer and more homogenous materials, good control over the final composition, and tailoring of the surface and pore characteristics of the product. Alkoxide derived gel-glasses of the system Sι0 2 -CaO-P 2 0 5 present an expanded compositional range of bioactivity over bioactive glasses made by melt processes. The difference in bioactive behavior relates directly to the structure of sol-gel derived materials. The gel-glasses have a much higher surface area, a higher concentration of silanol groups per unit area on the surface and a higher concentration of metastable three and four membered siloxane rings. The bioactivity is influenced by the texture of the material as well as the chemical composition. The gel-glasses are ideally suited as bone graft materials, due to their higher resorption rates in vitro and in vivo. Furthermore, the rate of soluble silicon species released during HCA formation, and the stimulation of bone growth are improved compared with those of the melt- derived bioactive glass. The compositions can be prepared, for example, by synthesizing an inorganic network by mixing metal alkoxides in solution, followed by hydrolysis, gelation, and firing to produce a porous matrix or a dense glass. The firing can be done at relatively high temperatures (600- 1100°C), and can also be done at lower temperatures (on the order of about 200 to 250°C). The sol-gel process used herein uses a four or more component system, including at least Sι0 2 , CaO, P 2 0 5 and a silver salt, for example, Ag 2 0 In one embodiment, the silver-containing sol- gel bioactive glass is produced as a gel network from tetraethoxysilane (TEOS), phosphorous alkoxide, calcium nitrate and silver oxide in water-ethanol solution. The process, and the types of reactions which typically occur in sol-gel formation, is described in more detail below. Aqueous solutions of SιQ 2 The first step of the sol-gel process typically involves mixing the precursor, silicon alkoxide, solvent (generally water), and an acid or alkaline catalyst. This step can dramatically affect the homogeneity of a multi-component gel, which is also influenced by the nature and reactivity of the precursors, the nature and solubility of the reactants in. the selected solvent, the concentration of the selected solvent, the sequence of addition, the pH and the time and temperature of the reaction. After mixing, the alkoxide precursor is hydrolyzed to silicic acid, which then condenses to yield the silica gel The hydrolysis reactions are shown below, where R is an alkyl group: Sι(OR) 4 + 4H 2 0 Sι(OH) 4 +4ROH RO-Sι(OR) 3 + HO-Sι(OR) 3 (OR) 3 Sι-0-Sι(OR) 3 +ROH HO-Sι(OR) 3 + HO-Sι(OR) 3 * (OR) 3 Sι-0-Sι(OR) 3 +H 2 0 Hydrolysis is believed to occur via bimolecular nucleophihc attack (S N 2) of water on the Si atom, and can be catalyzed by acids or bases. The nature of the alkoxide group (R) influences the rate of hydrolysis through inductive and steπc effects. When R is an electron- withdrawing group it accelerates the reaction, and if the R group is bulky it slows down the reaction rate. When producing a multi-component system, TEOS, rather than tetramethoxysilane (TMOS) (which only takes minutes to hydrolyze), is the chosen precursor m order to have better control on the rate of hydrolysis. Tetraethoxyphosphate (TEP) is used as a convenient source of phosphate monomers. Soluble metal salts, like nitrates, can also be used to introduce modifier atoms. The condensation is catalyzed by the same catalysts used m the hydrolysis and its reaction rate changes with the pH value of the solution. The pH conditions also affect how coarse and consolidated the resulting gel will be. The shape and the size of polymeric structural units are determined by the relative values of the rate constants for hydrolysis and polycondensation reactions. Fast hydrolysis and slow condensation favor formation of linear polymers; on the other hand, slow hydrolysis and fast polymerization results m larger, bulkier polymers. As the sol particles grow and collide condensation occurs and macroparticles form. The sol becomes a gel when it can support a stress elastically Agmg The agmg step involves maintaining the cast object for a period of time (typically from hours to days) immersed in liquid. During agmg, polycondensation continues along with localized dissolution and re-precipitation, until free reactive species and reactive sites have all reacted. This process, that decreases the porosity and strengthens the gel, is called syneresis; it causes the gel to shrink and expel the pore liquors. Along with syneresis, another phenomenon, called Ostwald ripening, takes place. This is an irreversible process involving preferential dissolution of high potential energy convex surfaces, followed by deposition on low energy concave surfaces. Thus, necks begin to form between primary particles and smaller pores are filled at the expense of the bigger ones. This coarsening process is usually slower compared with the syneresis, but it can affect the texture of the gel, particularly when the ag g takes place at high temperatures or high pH values Drying During drying, the liquid is removed from the interconnected pore network. Strong capillary stresses can develop and cause the gel to crack unless the drying process is controlled by decreasing the solid-liquid mterfacial tension. This can be achieved in a number of ways: by addition of surfactants; by hypercπtical evaporation which eliminates the solid-liquid interface; or by obtaining monodisperse pore sizes from controlling the rates of hydrolysis and condensation. Stabilization and densification Removal of the surface silanol groups results in a chemically stable porous material. This can be achieved using thermal and/or chemical methods. Chemical methods often involve modification of the silica surface by replacing the silanol groups with more hydrophobic and less reactive species (e.g., chlorides and fluorides). Heating above 400°C results in an irreversible dehydration due to the increasing elimination of isolated silanol groups and to the structural relaxation which takes place. In multi-component systems the calcination process also serves to degrade other species that are present in the gel (e.g., calcium nitrate, Ca(N0 3 ) 2 ). Nitrate species are undesirable in bioapphcations, and are also a source of m-homogeneity. They also remain m the specimen after drying and must be decomposed. Note that the decomposition of pure Ca(N0 3 ) 2 occurs at 561°C. Hence this temperature must be exceeded during successful stabilization if such groups are present Heating at temperatures between 800°C and 1500°C (depending on the initial porosity, mterconnectivity, atmosphere, and composition) will density the gel to become a consolidated glass with a density substantially equivalent to that of glasses made by conventional melting and casting. A usting the Pore Volume of the Compositions Suitable pore diameters are between 20 and 400 A. Pore diameters larger than 0.1 microns can be achieved using a sintering and/or foaming processes. The sintered structure may then be impregnated with a variety of materials, as discussed in more detail below. To aid in preparing glass compositions with high porosity, the glass composition can include a material which can be preferably leached out of the glass composition, and, in doing so, provide the composition with high porosity. For example, minute particles of a material capable of being dissolved in a suitable solvent, acid, or base can be mixed with or incorporated into the glass, and subsequently leached out. The resulting voids have roughly the same size as the particle that was leached out. The size of the pores and degree of porosity also depends on the amount of added material relative to the amount of glass. For example, if the leached material constituted about 80% of the glass, then the glass would be approximately 80% porous when the material was leached out. When leaching the glass composition, care should be taken not to leach out a significant amount of those components which add to the bioactivity of the glass, i.e., the calcium and phosphorus oxides, or the antibacterial properties of the glass, i.e., the silver ions. Preparation of Bioactive Glass Fibers Continuous fibers can be prepared, for example, by extruding the sol through a spinneret. The fibers can then be aged, dried, and thermally stabilized. Long fibers may be woven into a mesh, short fibers may be combined by mixing them with a degradable adhesive, such as a solution of carboxymethylcellulose (CMC). The resulting material is then heated in a kiln to smter the material and burn off the binder. Preparation of Bioactive Glass Coatmgs Coatmgs can be prepared using means well known to those of skill in the art, including dipping an article to be coated into an appropriate sol-gel solution which is then treated to form the sol gel, and spraying the article to be coated with particles of the bioactive glass. B Methods of Shaping the Fiber into Desired Structures After the composition has been spun into a fiber, for example in a spinneret, the resulting fiber can be shaped into desired structures. In one embodiment, the fiber is merely wound and can be used as a degradable suture material. In other embodiments, the fiber is mixed with various additional components, including polymeric materials, and shaped into desired articles of manufacture. The shaping can be performed via any acceptable means, including laser ablation, extrusion, molding techniques, and the like. The fibers can be formed into a mesh or fabric (woven or non- woven). The mesh can be used, for example, m wound healing and wound covering. In one embodiment, the fibers are woven into mats or other structures. The resulting material can be used to make structures useful, for example as bone graft substitutes and coverings for bony defects. The fibers can also be used to make three dimensional structures for preforms to be impregnated with polymers, for example biodegradable polymers. Such structures can be linked, covalently or lonically, to bioactive compounds, for example, growth factors, antibiotics, antivirals, nutrients and the like to enhance tissue repair and promote healing. The fibers can be incorporated into implanted materials, such as prosthetic implants, sutures, stents, screws, plates, tubes, and the like. The fibers (as well as particles) are also useful for tissue engineering applications. An advantage of using these fibers is that anti-bactenal properties can also be imparted to devices used for in vitro and ex vivo cell culture when the fibers are mcoφorated into tissue engineering devices. When the fiber has a relatively high porosity, it has a relatively fast degradation rate and high surface area, in comparison to non-porous bioactive glass fiber compositions The degree of porosity of the glass is between about 0 and 85%, preferably between about 10 and 80%), and more preferably, between about 30 and 60%. II. Formulations Including Bioactive Glass The form of the bioactive glass (particles, fibers, and the like) depends in large part on the intended use of the compositions Those of skill in the art can readily select an appropriate form for the bioactive glass for an intended use. Examples of applications of the silver- containing sol-gel derived bioactive glass compositions described herein include surgical treatment of peπodontal and osteomfections, inclusion in preparations to cure skm infections, use as a preservative m cosmetic preparations, introduction as antimicrobial agent in health care products and in detergents, and as preventative antimicrobial agents for surgery that involves the use of implanted biomateπals and/or devices. In addition to the bioactive glass composition, the formulations can include other therapeutic agents such as antibiotics, antivirals, healing promotion agents, anti-inflammatory agents, immunosuppressants, growth factors, anti-metabolites, cell adhesion molecules (CAMs), bone moφhogenic proteins (BMPs), vascularizmg agents, anti-coagulants, and topical anesthetics/analgesics The antibiotics can be topical antibiotics suitable for skm treatment. Examples of such antibiotics include but are not limited to. chloramphenicol, chlortetracycline, clyndamycm, choqumol, erythromycm, framycetm, gramicidin, fusidic acid, gentamicm, mafemde, mupiroicm, neomycm, polymyxm B, bacitracin, silver sulfadiazine, tetracyclme and chlortetracycline . Suitable antivirals include topical antivirals, such as acyclovir, and gancyclovir. Suitable anti-inflammatory agents include corticosteroids, hydrocortisone and nonsteroidal antmflammatory drugs. Suitable growth factors include basic fibroblast growth factor (bFGF), epithelial growth factor (EGF), transforming growth factors and β (TGF a and β ), platelet- derived growth factor (PDGF), and vascular endothehal growth factor/vascular permeability factor (VEGF/VPF)). Suitable topical anesthetics include benzocaine and hdocame. In one embodiment, the therapeutic agent is one which would otherwise cause an inflammation at the site at which it is delivered, and the bioactive glass compositions reduce the associated inflammation. For example, a number of compounds, for example, amme compounds, result in inflammation when administered topically, i.e., in a transdermal patch. In addition, the bioactive glass may be combined with any biocompatible material, such as biodegradable polymer like polylactic/glycohc acid to form a composite material for accelerating wound healing. The proportion of other therapeutic agents varies according to the agent and the nature of the application. However, the preferred proportions are such that the amount of the agent administered to the patient is m a dosage range accepted withm standard medical care. III. Articles of Manufacture Including Bioactive Glass The silver-containing, sol-gel derived bioactive glass compositions can be incoφorated into implanted materials, such as prosthetic implants, sheets, pms, valves, sutures, stents, screws, plates, tubes, and the like, by mcoφoratmg bioactive glass particles into the implanted materials. The compositions can be moldable or machinable. Table 2, below, shows a relation between the form of the bioactive glass composition and the intended function. This table is not intended to limit the type of form which can be used for an intended function, merely to exemplify types of forms and matching functions. The compositions described herein can be m any of these forms. Table 2 The articles of manufacture are imparted with anti -bacterial properties via the mcoφoration of the silver ions into the bioactive glass, which will allow the articles to be implanted, or used to culture cells, with a reduced likelihood of bacteriological contamination. Cell Growth and Culture There are many solutions used for culturmg cells. These include Dulbecco's minimal essential media, Hank's balanced salt solution, and others These solutions are essentially lsotomc with the cells to be cultured. A problem associated with cell culture is often the growth of bacteria in culture along with the desired cells Bacterial growth can be minimized by coφorating the bioactive glass compositions into matrices used in cell culture and tissue engineering applications. V. Methods for Improving Wound Healing The silver-containing, sol-gel derived bioactive glass fibers, particles and/or coatmgs are capable of dramatically reducing the amount of time necessary for wound healing to occur. Implants including the fibers, particles or coatings, preferably highly porous fibers or particles, alone or in combination with other anti-bactenal agents, can augment the natural healing process. The effectiveness of the fibers, particles and coatings described herein is most dramatically illustrated in immune compromised patients whose ability to heal wounds is somewhat suppressed. In one embodiment, the fibers and/or particles are used to fill voids, including voids created during medical procedures. For example, during a root canal operation, the hollowed- out tooth can be filled with a composition including bioactive glass fibers and/or particles. This will help prevent bacterial infection until the tooth is ultimately filled. Also, bioglass- contaimng compositions can be used to fill the pockets that can develop between the teeth and gums. Compositions including bioactive glass fibers and/or particles can be used to fill voids present in aneurysms, and prevent bacterial growth inside the filled void Other voids which can be filled include those formed surgically, such as removal of a spleen, ovary, gall bladder, or tumor. VI. Methods for Grafting Skin The methods for grafting skm involve applying meshes or fabrics including the silver- containing, sol-gel derived bioactive glass fibers, particles and/or coatings to either the graft site or donor tissue before it is placed in its intended location. Those interested m a detailed description of skm grafting are referred to "Skm Grafts," in Selected Readings in Plastic Surgery, Vol. 7, no. 2, P. L. Kelton, MD, Baylor University Medical Center (1992). The graft may also be further treated with a topical carrier prior to placement The application of bioactive glass to grafts is intended to increase the likelihood that the graft will "take" and mcoφorate in the host bed. It is intended that the bioactive glass will act as an intermediary bond between the host and graft tissue, suppress the overall inflammatory response which could lead to rejection, as well as accelerate the overall healing process which will lead to a faster and more successful acceptance. The bioactive glass fibers, particles and/or coatings can be administered locally to a surgical site to minimize post-surgical adhesions. The compositions can optionally be incoφorated into a polymeric material which is applied to the surgical site Alternatively, the bioactive gel-glass can be used as a coating on polymeric materials which is applied to the surgical site Preferably, the polymeric material is biodegradable Suitable polymeric materials for this puφose are disclosed, for example, m U.S. Patent No 5,410,016 to Hubbell et al., the contents of which are hereby incoφorated by reference. Other materials suitable for this puφose, such as Interceed ® , agarose and crosslmked algmate, are well known to those of skill Biomedical implants are often associated with inflammation at the site of implantation. Incoφoration of the bioactive glass fibers described herein, in particular, the highly porous bioactive glass fibers, into the implants, especially on the surface of the implants, can greatly reduce the inflammation associated with the implants. This can be especially useful in suture materials to minimize the inflammation associated with these materials The anti-bactenal properties of the compositions also allow the sutures to minimize the infection surrounding the suture site. The present invention will be more clearly understood with reference to the following non-hmitmg examples. EXAMPLES Example 1 : Preparation of Silver-Containing Sol-Gel Derived Bioactive Glasses Silver-doped 58S sol-gel Bioglass ® has been prepared by a sol gel method. The textural characteristics of the material (surface area, pore volume, and average pore diameter) were measured by gas-soφtion. The antimicrobial action of the silver-doped gel-glass was compared with a control culture with no gel glass. The bioactivity and dissolution behavior in simulated body fluid of the gel-derived specimen has also been monitored. Materials preparation A bioactive gel-glass of the three-component CaO-P 2 0 5 -Sι0 2 system, namely the 58S, in which 2% (molar) Ag 2 0 has been introduced by substitution of CaO, has been formed, hereby referred to as 58S7Ag. The numbers refer to the weight percentage of silica and silver oxide. The mix compositions of the material, as well as the non-silver containing counteφart 58S, are listed in Table 3. The 58S7Ag specimen was always handled in the dark, using a safe light, and was stored m a black-box to preserve it in its oxidized state. Table 3 - Composition of the materials produced in moles and weight Hydrolysis and copolvmenzation The following compounds were added to deionized (DI) water obtained from an instant purifier Micromeg Elgostat in sequential order; 2N nitric acid (HN0 3 ), tetraethoxysilane (TEOS) 99% purity, triethoxyphosphate (TEP) 99% purity A.C.S., Ca(N0 3 ) 2 -4H 2 0 99% purity A.C.S., and AgN0 3 99.99% purity. After two hours of moderated stirring the mixture was poured into polymethylpentane pots, hermetically sealed, and left to gel at room temperature for two days. Agmg The pots containing the gels were transferred to an oven at 60°C Agmg took three days. Drying The aged gels were placed on a watch glass in a drying chamber above 250 ml of DI water. Thus, the near equilibrium drying conditions were realized, in which the pore liquor evaporating from the gel was supported by the vapor pressure of the water. The drying schedule involves three stages, listed in Table 4. The temperature gradient between each step was 0.1°C/mιnute. Table 4 - Heating program for drying step. Stabilization The stabilization was carried out in a box furnace at 450°C for 19 hours, Textural characterization Surface analysis The textural characterization was performed on a six port Quantachrome AS6 Autosorb and two single port Quantachrome AS I Autosorb gas soφtion systems. The instruments determined isotherms volumetπcally at 77.4 K. The adsoφtive gas was nitrogen, N 2 , of 99.999% purity. The cross sectional area of adsorbed nitrogen molecules was taken to be 0.162 nm 2 for the puφoses of specific surface area calculations. Prior to nitrogen soφtion, all samples were degassed under vacuum pressure lower than 1 Pa. at 25°C for 19 hours to remove physically adsorbed material from their surfaces Each isotherm comprised a minimum of 20 adsoφtion and 20 desoφtion points measured at equilibrium. At least four adsoφtion points in the relative pressure range 0.05 < P/P 0 < 0.25 (where P 0 1 is the saturated vapor pressure) were used in the calculation of the BET surface area in each case. It was ensured that the slope and intercept of the BET plots were positive and that the product moment correlation coefficients were not less than 0.9999. Two isotherms were collected for each sample to ensure that the data was representative. Data from the second isotherms has been used in the evaluation of the textural parameters reported here. The specific surface areas and pore volumes were estimated in relation to the masses of the samples. Skeletal density The skeletal density (true density) was measured by helium ultrapycnometry using a Quantachrome helium Ultrapycnometer 1000. The instrument uses the ideal gas equation PV=nRT to measure the volume occupied by the sample. The mass of the samples was measured using a four-decimal place digital balance. The instrument was calibrated immediately before running the analysis. The measurements were repeated 80 times to ensure reproducibihty. Treatment of Data The most widely employed model for the evaluation of specific surface area is the BET method which is based upon the measurement of quantities of gas physisorbed onto a surface at equilibrium pressure. This method yields reliable results for isotherms of type II and IV (according to Brunauer and IUPAC classifications). Estimates of specific pore volume were obtained from the amount of nitrogen taken up by the samples in the range 0.9947 < P/P 0 < 0.9956 Pore size distributions were calculated from desoφtion data by the BJH method (Barret E.P., Jomer L.G. & Halenda P.P., J. Am, Chem. Soc, 73, 1951, pp. 373-380). The standard deviations of the means were calculated of-the specific surface area, specific pore volume, mean pore diameter, modal pore diameter, and skeletal density have also been evaluated. The 95% confidence limits were also estimated. It was assumed that the sample population conformed to a Gaussian distribution. EDAX analysis Since the material looked visibly non homogeneous (white, reddish and black shades were observable) three pieces of three different shades of color were selected, coated with carbon and subjected to qualitative and quantitative energy dispersive X-ray analysis (EDAX). The principle behind this technique is the following: an incident electron beam causes atoms to undergo an energy transition to a higher electronic state; the X ray radiation emitted to return to their fundamental electronic state, which is characteristic for each element, is then collected by the instrument. In vitro bioactivity and dissolution study Preparation of simulated body fluid (SBF) solution All the chemicals required for this preparation had the highest purity grade available. The reagents were added to 700 ml of DI water, at 36.5°C under constant stirring, in the following order: 7.996g of NaCl, 0.35g of NaHC0 3 , 0.224g KC1, 0.228g of K 2 HP0 4 -3H 2 0, 0.305g of MgCl 2 -6H 2 0, 40ml of IN HCl, 0.368g of CaCl 2 , 0.071g of Na 2 S0 4 , and 0.057g of (CH 2 OH) 3 CNH 2 . The pH was then adjusted with IN HCl to 7.25, and finally, the solution was made up to 1 liter in a volumetric flask. The solution was stored at 40 °C in polyethylene bottles for no longer than 1 month. Bioactivity test Immersion of powder or bulk samples of bioactive glass in SBF (which resembles the composition of human blood plasma) initiates the surface reactions that lead to the deposition of a bone-like HCA layer. The results are shown in Table 5. The kinetics of HCA formation observed with this in vitro experimental method correlate adequately with the results of in vivo studies. Table 5 - Ionic concentrations of the SBF solution and human blood plasma in mmol/CC. 58S7Ag specimens (cuboids weighting ~60mg each) were immersed in 10 ml of SBF in PMP containers, which were sealed and placed in a water bath at 37°C, for different time intervals. Each experiment was carried out in triplicate. The specimens were recovered at the required times and dπed in an oven at 60°C for at least 4 hours. The immersion times vaπed between 1 hour and 7 days. The dissolution of the constituents of the gel-glass was studied with quantitative Inductively Coupled Plasma analysis (ICP) which is based on atomic emission spectrometry. The principle of this analytical technique is the following: a solution of the element whose concentration is to be determined, is introduced into the ICP ionizing torch as aqueous aerosol, the light emitted by the atoms or ions is detected by the spectrometer and the concentration is computed by comparison with a standard solution. The release of Si, Ca, P, and Ag ions into the SBF solution was monitored using this technique. The instrument detection limits for the elements of interest were respectively 0.050, 0.100, 0.200, and 0.020 ppm. The growth of the HCA layer was monitored using a Midac Series FTIR spectrophotometer The spectra were recorded between 400 and 1600cm "1 , measuring the diffuse radiation reflected by the surface of the bulk sample This is a non destructive analysis which does not require the preparation of a KBr disc. Antibacterial tests 58S7Ag was ground to powder with a mortar and pestle and sieved within the particle size range 90-7 lOμm. The antimicrobial effect of the powder samples was investigated on liquid cultures of E. colt (strain MG1655). The growth medium for the bacteria was LB, a πch medium prepared with bacto-tryptone, yeast extract, and NaCl. A 5 ml starter culture of E. coh was incubated for 6 hours. lOOμl of this culture were then inoculated m 5 ml of LB medium containing lOOmg and 200mg of 58S7Ag. A control sample, containing only the cell inoculum in LB, was also cultured. Each experiment was carried out in triplicate. The cultures were put in an orbital shaker and incubated at 37°C for 20 hours. The antibacterial action was estimated from the percentage of growth of E. Coli. The concentration of cells in suspension was calculated from optical density measurements of the turbidity of the solutions using a spectrophotometer reading the absorbance at 600nm The absorbance values have been "normalized" by subtracting the optical density readings of the non-moculated LB culture medium. Statistical treatment of data The measurements of the optical densities of the sample populations (E coh + 58S7Ag) were compared with the control culture population using the assumption that their standard deviations were not significantly different. A "pooled" estimate of standard deviation S is calculated using the formula: (n, + n 2 - 2) Equation 7 where s, and s 2 are the two standard deviations to compare. The value oft (at n, + n 2 - 2 degrees of freedom) is given by: SV 1/n, = 1/n, Equation 8 RESULTS EDAX analysis EDAX spectrum were obtained, which confirmed the presence of all the species introduced duπng the mixing step of the sol-gel process. Peaks observed at 1.760, 2,020, 3.020, as well as two peaks observed around 3.720 keV represent Si, P, Ag, and Ca respectively. Irrespective of the m-homogeneous appearance of the material, quantitative EDAX analysis showed an overall homogeneity of composition of the 58S7Ag (Table 6). The relative concentrations of network modifiers Ca, P, and Ag are lower than is indicated by the nominal mix composition, due to leaching during gelling and drying. Table 6 - Quantitative EDAX analysis on three different pieces of 58S7Ag. Textural Characterization Adsoφtion and desoφtion isotherms for nitrogen were taken of the 58S7Ag samples. The isotherms were representative of those collected for all of the 58S7Ag samples, and were of type IV, indicating that the samples are mesoporous (i.e. they possess pore diameters in the range 20 to 500 A). Hysteresis in the multilayer region of the isotherms, denoted by the deviation in pathway of the adsoφtion and desoφtion data, is associated with capillary condensation in the mesopore stricture. The hysteresis loops are of type HI (formerly type A) which indicates the presence of cylindrical pores of narrow pore size distribution. The modal pore diameters for 58S7Ag are approximately 169 A respectively. Hence, the modal pore radii, ~ 85 A, are notably smaller than the mean pore radii, 135.6 A. The difference between the two quantities is believed to arise from a combination of factors: deviation from perfect cylindrical geometry, the volume associated with the junctions of the pores, and the existence of a small number of large pores. The textural features of 58S7Ag are shown below m Table 7 Table 7 - The textural features of 58S7Ag. 2V=/S„ The calculated value of the bulk density of 58S7Ag is 1.0759 g/cm 3 , which denotes a highly porous silica matrix. Bioactivity and dissolution behavior FTIR spectra of 58S7Ag as a function of residence time in SBF were taken. The spectra show peaks at 605 and 567 cm "1 corresponding to the bending vibrations of the phosphate P-O bonds. The broad peak around 460 cm ' arises from to the bending vibration of amoφhous silica and the peak at 1100 cm ' is assigned to the Sι-0 stretching vibration mode. The bioactivity test in vitro for the 58S7Ag showed a high rate of HCA deposition. The growth of hydroxyapatite is already visible after 3.5 hours and increases with time while silica peaks become less predominant, as shown by the FTIR spectra. Ionic concentration curves were obtained from ICP analysis, and these curves were consistent with the FTIR results. Each data point plotted was the mean of three measurements. After 48 hours there was a notable decrease in the phosphate concentration, indicating the precipitation of hydroxyapatite. The silicon dissolution rate is still high after the first 3 days. The very slow release of the silver ion into the solution suggests that it is strongly chelated by the silicate network. The maximum silver concentration observed after 7 days was still lower than 30μM, which is considered safe from the toxicological stand point Antibacterial properties The effect of 58S7Ag on E. coli MG1655 after 20 hours of incubation was determined The intensity of absorbance at 600 nm is a measure of optical density, which, m turn, is a measure of the E coh cell-concentration. The results indicate that the presence of 58S7Ag (brown column) greatly inhibited the growth of E coh MCT1655, resulting in a cell concentration 85% lower than the control after 20 hours of incubation. The Ag-doped gel-glass 58S7Ag exhibited a strong antimicrobial response. ICP data reveal that the release of silicate species from 58S7Ag continues well after the first three days in SBF. The very slow release of silver ions indicates that they are strongly chelated by the silicate network. Rapid dissolution kinetics may be required to obtain an effective antimicrobial action m clinical applications, to prevent the development of antimicrobial resistance. In some embodiments, it may be preferable to prepare silver-doped bioactive gel-glass in which the silver ion is not as strongly bound to the silica matrix. This can be achieved by using a lower stabilization temperature, gel glasses with a larger pore size, a larger volume fraction of pores or a larger concentration of silver dopant. The percentage composition of the bioactive system Sι 2 0-Ca0-P 2 0 5 -Ag 2 0 determined with quantitative EDAX analysis shows that the actual content of network modifiers (CaO, P 2 0 5 , Ag 2 0) in the final product is different from that of the nominal mix composition. This phenomenon may be attributed to the incomplete hydrolysis of TEP and the leaching of soluble ions from the silica network during gelling, washing, and drying. The sol-gel route has been successfully used to produce a new composition of bioactive gel-glass containing silver oxide The resulting material is a porous gel-glass having the desired textural characteristics: a mesoporous structure with cylindπcally shaped pores which are monomodally dispersed. An in vitro bioactivity test has shown that the introduction of 3 wt.% silver oxide to the three-component system, Sι0 2 -CaO-P 2 0 5 , does not inhibit bioactivity. The dissolution study has confirmed that the material is capable of releasing silicate species (which is very important for its mitogemc effect in vivo) even after the first three days of immersion. The rate of dissolution of silver ions is relevant to eventual clinical applications, since the prerequisite of an effective, topical antimicrobial agent is an immediate and concentrated release of that agent. The dissolution kinetics observed indicated a slow and constant rate of dissolution over a period of seven days Modification to the sol-gel process may yield a material that can control the release kinetics of silver ions and be tailored for a specific clinical application

Claims: WHAT IS CLAIMED IS: 1. A composition comprising silver-containing sol-gel derived bioactive glass. 2. The composition of claim 1, in the form of particles, fibers or coatmgs. 3. The composition of claim 1, further comprising one or more therapeutic agents. 4. The composition of claim 3, wherein therapeutic agent(s) are selected from the group consisting of healing promotion agents, growth factors, anti-inflammatory agents and topical anesthetics. 5. The composition of claim 2, wherein the therapeutic agent is a topical antibiotic. 6 The composition of claim 5, wherein the topical antibiotic is selected from the group consisting of chloramphemcol, chlortetracycline, clyndamycm, clioqumol, erythromycm, framycetm, gramicidin, fusidic acid, gentamicm, mafemde, mupiroicm, neomycm, polymyxm B, bacitracm, silver sulfadiazme, tetracychne, chlortetracycline and combinations thereof. 7. The composition of claim 1, wherein the porosity is between 10 and 80 percent. 8. The composition of claim 1, wherein the bioactive glass has a composition by weight percentage : Component Percent Sι0 2 45-86 CaO 6-50 PA 0-12 Ag 2 0 0.1-12 A1A 0-3 CaF 2 0-25 BA 0-20 κ 2 o 0-8 MgO 0-5 Na 2 0 0-20 9. The composition of claim 1, wherein the bioactive glass has a composition by weight percentage: Component Percent Sι0 2 45-86 CaO 10-36 PA 3-12 Ag 2 0 3-12 CaF 2 0-25 B 2 0 3 0-10 K 2 0 0-8 MgO 0-5 10. The composition of claim 1, wherein the particles, fibers or coatings have a pore size in the range of between about 20-400 angstroms. 11. The composition of claim 1. wherein the particles, fibers or coatmgs have a surface area in the range of between about 20-400 m 2 /g. 12. A method for treating wounds and burns comprising contacting a wound with an effective wound healing amount of the composition of claim 1. 13. A method for grafting skm comprising applying the composition of claim 1 to a graft site, the donor tissue, or both. 14. The method of claim 13, further comprising the application of a topical antibiotic to the graft site, the donor tissue, or both. 15. A wound or burn dressing comprising a bandage comprising the particles, fibers or coatmgs of claim 1 and a topical antibiotic. 16 The composition of claim 1 , wherein the composition has been combined with a biocompatible, biodegradable material to form a composite material 17. The composition of claim 1, wherein the composition is part of a matrix used for tissue engineering.

Inventors: BELLANTONE MARIA, COLEMAN NICHOLA J, HENCH LARRY L, BELLANTONE, MARIA, COLEMAN, NICHOLA, J., HENCH, LARRY, L.
Applicants: BELLANTONE MARIA, COLEMAN NICHOLA J, HENCH LARRY L, USBIOMATERIALS CORP, BELLANTONE, MARIA, COLEMAN, NICHOLA, J., HENCH, LARRY, L., USBIOMATERIALS CORPORATION
Application year: 2000
Main classification: A61K9
IPC codes: A61K9, A61L17, A61L27, C03C1, C03C3, C03C4, C03C8, C03C13, C03C14