US20120035740A1 - Biodegradable implant and method for manufacturing same - Google Patents

Biodegradable implant and method for manufacturing same Download PDF

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US20120035740A1
US20120035740A1 US13/265,694 US201013265694A US2012035740A1 US 20120035740 A1 US20120035740 A1 US 20120035740A1 US 201013265694 A US201013265694 A US 201013265694A US 2012035740 A1 US2012035740 A1 US 2012035740A1
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biodegradable implant
porous structure
magnesium
implant
biodegradable
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Ja-Kyo Koo
Seok Hyun-Kwang
Seok-Jo Yang
Yu-Chan Kim
Sung-youn Cho
Jong-Tack Kim
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U&I Corp
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    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/02—Inorganic materials
    • A61L27/04—Metals or alloys
    • A61L27/047—Other specific metals or alloys not covered by A61L27/042 - A61L27/045 or A61L27/06
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/40—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material
    • A61L27/42—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having an inorganic matrix
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/40—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material
    • A61L27/42—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having an inorganic matrix
    • A61L27/427—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having an inorganic matrix of other specific inorganic materials not covered by A61L27/422 or A61L27/425
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/40—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material
    • A61L27/44—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having a macromolecular matrix
    • A61L27/446—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having a macromolecular matrix with other specific inorganic fillers other than those covered by A61L27/443 or A61L27/46
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/40—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material
    • A61L27/44—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having a macromolecular matrix
    • A61L27/48—Composite materials, i.e. containing one material dispersed in a matrix of the same or different material having a macromolecular matrix with macromolecular fillers
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/50—Materials characterised by their function or physical properties, e.g. injectable or lubricating compositions, shape-memory materials, surface modified materials
    • A61L27/56—Porous materials, e.g. foams or sponges
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/50—Materials characterised by their function or physical properties, e.g. injectable or lubricating compositions, shape-memory materials, surface modified materials
    • A61L27/58—Materials at least partially resorbable by the body
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/11—Making porous workpieces or articles
    • B22F3/1121—Making porous workpieces or articles by using decomposable, meltable or sublimatable fillers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F3/26—Impregnating
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/06—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture

Definitions

  • the present invention relates to a biodegradable implant and a method of manufacturing the same, and more particularly to a biodegradable implant, whose biodegradation rate is easily controlled, the strength and an interfacial force to bone tissue of which are high, in which a rate of bone formation is increased, and that has simultaneously improved corrosion resistance and mechanical properties, and to a method of manufacturing the same.
  • Typical materials used in implants to be used in medical treatment include metal, ceramic and polymer.
  • metallic implants have superior mechanical properties and processability.
  • metallic implants are disadvantageous because of stress shielding, image degradation and implant migration.
  • ceramic implants have superior biocompatibility compared to the other implants.
  • ceramic implants are easily broken by external impact, and are difficult to process.
  • polymeric implants have relatively weak strength compared to the other implant materials.
  • porous implants are being developed which may accelerate the formation of bone tissue upon insertion into the human body and may decrease Young's modulus to prevent stress shielding.
  • porous implants have low mechanical strength and are weak to external impact.
  • biodegradable implants which need not be removed after being inserted into the human body to achieve their desired purpose.
  • the study of medical applications using such a biodegradable material has already begun since the middle of the 1960s and is mainly focused on using polymers such as polylactic acids (PLA), polyglycolic acid (PGA) or a copolymer thereof including PLGA.
  • biodegradable polymers have low mechanical strength, produce acids upon decomposition, and have the disadvantage that it is difficult to control their biodegradation rate, and thus they have limited applications.
  • the biodegradable polymers are difficult to apply to orthopedic implants that have to withstand a strong load or dental implants because of the properties of polymers having low mechanical strength.
  • some biodegradable materials are being studied to overcome the problems of the biodegradable polymers.
  • Typical examples thereof include ceramic such as tri-calcium phosphate (TCP), combination materials of biodegradable polymer and biodegradable hydroxyapatite (HA), etc.
  • biodegradable implants should be very strong because part or all of it have to withstand a load when used into the human body.
  • a biodegradable implant is further subjected to additional processes including rapid cooling, extrusion, and heat treatment so that the framework of the implant is made fine and internal residual stress should be controlled.
  • the alloy composition of a metal used for a biodegradable implant should be appropriately designed by changing constituent elements or content thereof. As such, changing the alloy composition may be typically performed by adjusting the amounts of the elements that are added. As the amounts of elements added to the alloy increase, mechanical strength is enhanced.
  • the metal for the implants may easily create a galvanic circuit that increases the corrosion rate attributable to an increase in the non-uniformity of the composition thereof and the non-uniformity of a fine framework, undesirably increasing the corrosion rate of implants.
  • an object of the present invention is to provide a biodegradable implant whose biodegradation rate may be controlled.
  • Another object of the present invention is to provide a biodegradable implant which may overcome problems of conventional porous implants such as low mechanical strength and poor impact resistance.
  • a further object of the present invention is to provide a biodegradable implant whose corrosion resistance and mechanical properties have been simultaneously improved.
  • Still a further object of the present invention is to provide a biodegradable implant in which a rate of bone formation may be increased, and with the passing of a predetermined period of time after surgery, a biodegradable metal material charged in pores has disappeared and an osseous replacement has taken place.
  • an aspect of the present invention provides a biodegradable implant comprising magnesium, wherein the magnesium contains as impurities (i) manganese (Mn); and (ii) one selected from the group consisting of iron (Fe), nickel (Ni) and mixtures of iron (Fe) and nickel (Ni), wherein the impurities satisfy the following condition: 0 ⁇ /(i) ⁇ 5, and an amount of the impurities is 1 part by weight or less but exceeding 0 parts by weight based on 100 parts by weight of the magnesium.
  • another aspect of the present invention provides a method of manufacturing a biodegradable implant, comprising a) providing magnesium containing as impurities (i) manganese (Mn); and (ii) one selected from the group consisting of iron (Fe), nickel (Ni) and mixtures of iron (Fe) and nickel (Ni), wherein the impurities satisfy the following condition: 0 ⁇ (ii)/(i) ⁇ 5, and an amount of the impurities is 1 part by weight or less but exceeding 0 parts by weight based on 100 parts by weight of the magnesium; and b) forming the magnesium.
  • a biodegradable implant comprising a magnesium alloy represented by Chemical Formula 1 below comprising based on the total weight thereof, 23 wt % or less but exceeding 0 wt % of Ca; 10 wt % or less but exceeding 0 wt % of X; and a remainder of Mg:
  • X is Mn or Zn.
  • another aspect of the present invention provides a method of manufacturing a biodegradable implant, comprising i) providing the magnesium alloy; and ii) forming the magnesium alloy.
  • another aspect of the present invention provides a method of manufacturing a biodegradable implant, comprising applying ultrasound to the biodegradable implant comprising magnesium.
  • another aspect of the present invention provides a biodegradable implant, comprising, based on the total weight thereof, 10 wt % or less but exceeding 0 wt % of manganese; 1 wt % or less but exceeding 0 wt % of iron; and a remainder of a metal comprising magnesium.
  • another aspect of the present invention provides a biodegradable implant, comprising, based on the total weight thereof, 90 wt % or less but exceeding 0 wt % of magnesium oxide (MgO); and a remainder of a metal comprising magnesium.
  • MgO magnesium oxide
  • a biodegradable implant can be advantageously present for a long period of time in vivo because its biodegradation rate is controlled to be very low.
  • the biodegradable implant includes a porous structure
  • blood vessels that pass through pores are formed, thus increasing the rate of bone formation and decreasing Young's modulus thereby reducing stress shielding.
  • the biodegradable implant can have enhanced mechanical strength and impact resistance.
  • the biodegradable implant can be simultaneously improved in terms of corrosion resistance and mechanical properties.
  • the implant according to the present invention is adapted to be used in bone replacements or treatment for bone, and can be used for orthopedics, dental care, plastic surgery or blood vessels.
  • FIG. 1 is a graph showing the hydrogen evolution amount in relation to the immersion time of the implant samples of Example 1 and 2 and Comparative Examples 1;
  • FIG. 2 is a graph showing results of evaluating mechanical strength of the implant samples of Examples 3 and 4 and Comparative Example 3 before extrusion;
  • FIG. 3 is a graph showing results of evaluating mechanical strength of the implant samples of Examples 3 and 4 and Comparative Example 3 after extrusion;
  • FIG. 4 is a graph showing the hydrogen evolution rate in relation to the immersion time of the implant samples of Examples 3 and 4 and Comparative Example 3;
  • FIG. 5 is a graph showing the hydrogen evolution rate in relation to the immersion time of the implant samples of Examples 4 to 6.
  • FIG. 6 is a graph showing the hydrogen evolution amount in relation to the immersion time of the implant samples of Examples 7 to 11 and Comparative Examples 2 and 4;
  • FIG. 7 is a graph showing the hydrogen evolution amount in relation to Zn content
  • FIG. 8 is an electron microscope image showing the surface of the implant sample of Example 7 immersed in a biomimetic solution for 61 hours;
  • FIG. 9 is an image showing the surface of the implant sample of Example 7 immersed in a biomimetic solution for 61 hours as analyzed using EDS;
  • FIG. 10 is an image showing the implant sample of Example 7 which is immersed in a biomimetic solution for 61 hours and from which a corrosion material was removed;
  • FIG. 11 is an image showing the cross-section of the implant sample of Example 7 immersed in a biomimetic solution for 61 hours;
  • FIG. 12 is an enlarged image of the image of FIG. 11 ;
  • FIG. 13 is of WDS (JXA-8500F, available from JEOL) images showing the implant sample of Example 7 immersed in a biomimetic solution for 61 hours;
  • FIG. 14 is an image showing the cross-section of the implant sample of Example 8 immersed in a biomimetic solution for 61 hours;
  • FIG. 15 is of WDS (JXA-8500F, available from JEOL) images showing the implant sample of Example 8 immersed in a biomimetic solution for 61 hours;
  • FIG. 16 is a graph showing the hydrogen evolution rate in relation to the immersion time in two implant samples of Example 8 one of which is treated with ultrasound and the other one of which is not treated with ultrasound after which they are immersed in a biomimetic solution;
  • FIG. 17 is a graph showing the hydrogen evolution amount in relation to the immersion time in the implant sample of Example 8 treated with ultrasound and then immersed in a biomimetic solution;
  • FIG. 18 is a graph showing the hydrogen evolution amount in relation to the immersion time of the implant samples of Examples 12 ⁇ 14;
  • FIG. 19 is of images showing the size of crystal grains of the implant sample of Example 14 before extrusion
  • FIG. 20 is a graph showing the hydrogen evolution amount in relation to the immersion time before and after extrusion of the implant sample of Example 14.
  • FIG. 21 is a photograph showing swelling due to the generation of hydrogen gas in a rat into which the implant sample of Comparative Example 4 is inserted.
  • a biodegradable implant comprises magnesium (Mg), wherein the Mg contains, as impurities (i) Mn and (ii) one selected from the group consisting of Fe, Ni and mixtures of Fe and Ni, wherein the impurities satisfy the following condition: 0 ⁇ /(i) ⁇ 5, and an amount of the impurities is 1 part by weight or less but exceeding 0 parts by weight based on 100 parts by weight of the magnesium.
  • the impurities satisfy the following condition: 0 ⁇ /(i) ⁇ 0.5. If the impurities satisfy the condition, the biodegradation rate is controlled to be maximally low thus increasing corrosion resistance. Thereby, implants may be present for a longer period of time in vivo.
  • Ni and Mn are contained in the impurities, Ni causes an allergic reaction in the human body and increases the corrosion rate of pure Mg.
  • Ni content is preferably 100 ppm or less, and more preferably 50 ppm or less.
  • the Mg may further include aluminum (Al) as an impurity.
  • a biodegradable implant resulting from charging Mg containing the above impurities in the pores of a porous structure.
  • the pores of the porous structure preferably have a size of 200 ⁇ 500 ⁇ m, and the pore size may be adjusted depending on the application field using methods typically used in the art. If the pore size falls within the above range, it is easy to allow blood vessels responsible for supplying nutrients, minerals and ions to pass through the pores.
  • the porous structure may have a porosity of 5 ⁇ 95%.
  • the porosity means a volume ratio of pores relative to total volume. In the case where the strength required of a target is high, the porosity may be decreased so that the strength of a porous structure is enhanced. For example, the case where a porous structure is made of tantalum having high strength or merely functions to fill the cavities of lost bone, high porosity thereof does not cause problems.
  • the porous structure may comprise one or more selected from the group consisting of a metal, a ceramic, and a polymer.
  • a metal one or more selected from the group consisting of titanium or a titanium alloy, a cobalt-chromium alloy and stainless steel may be used.
  • a ceramic one or more selected from the group consisting of calcium phosphate, alumina, zirconia and magnesia may be used.
  • the porous structure is made of a polymer, one or more selected from the group consisting of polyethylene, polylactic acids (PLA), polyglycolic acid (PGA) and a copolymer thereof including PLGA may be used.
  • the porous structure may comprise the above polymer
  • an acid that is biodegradable is generated so that the pH may decrease.
  • Mg may increase the pH while it is decomposing, and thus when the rate of decomposition of the polymer and Mg is controlled, an additional effect of arbitrarily adjusting the pH in vivo may be expected.
  • the biodegradable implant may be used for orthopedics, dental care, plastic surgery or blood vessels.
  • the above implant may be utilized for an interbody spacer for the spine, a bone filler, a bone plate, bone pin, bone screw, scaffold, Stent and artificial dental root.
  • the method of manufacturing the biodegradable implant comprises a) providing Mg containing as impurities (i) Mn and (ii) one selected from the group consisting of Fe, Ni and mixtures of Fe and Ni, wherein the impurities satisfy the following condition: 0 ⁇ /(i) ⁇ 5, and an amount of the impurities is 1 part by weight or less but exceeding 0 parts by weight based on 100 parts by weight of the magnesium; and b) forming the magnesium.
  • Mg is preferably provided in the form of being molten.
  • a) is performed by melting Mg in an inert gas atmosphere such as argon (Ar) that does not react with Mg or in a vacuum.
  • providing the molten Mg in a) may be carried out using a variety of processes, including a resistance heating process for generating heat by applying electricity to a resistor, an induction heating process that allows current to flow in an induction coil, or a laser- or focused light-based process.
  • a resistance heating process is particularly useful. It is preferred that the molten alloy (i.e. a melt) be stirred so that the impurities are well mixed when the Mg melts.
  • a) in the case where there is provided a biodegradable implant obtained by filling the pores of a porous structure with the Mg alloy, a) may include a-1) preparing a porous structure; and a-2) filling the pores of the porous structure with the Mg alloy.
  • the porous structure may comprise one selected from the group consisting of a metal, a ceramic and a polymer.
  • a metal is prepared in the form of powder or a wire.
  • the metal powder or wire is prepared into a preform (a Green preform).
  • the preform may be obtained using a sintering process or a modified sintering process.
  • the production of the preform using a sintering process is as follows: first, metal powder or wire is placed in a vessel, or is pressed by an appropriate force of 100 MPa or less so as to have weak strength, after which the metal having weak strength is maintained at a temperature of 2/10 ⁇ 9/10 of the melting point of the metal so that the powder or wire respectively coheres thus obtaining a preform having mechanical strength.
  • the production of the preform using a modified sintering process is as follows: first, metal powder or wire is placed in a conductive vessel such as graphite vessel, and high current is then applied to the conductive vessel so that heat is instantly generated on the contact portion of the metal powder or wire thus preparing a sintered body, which is then formed into a preform.
  • a conductive vessel such as graphite vessel
  • a-1) is described below for the case of using a metal and a polymer to prepare the porous structure.
  • a metal is prepared in the form of powder or a wire. Subsequently, the metal powder or wire is mixed with a polymer, and in the course of increasing the temperature, the polymer decomposes and disappears at low temperature and the metal powder or wire is sintered at high temperature, thus obtaining a preform having the appropriate mechanical strength.
  • the porosity and the strength of the sintered body are determined by the sintering temperature, the pressure, the ratio of the polymer and metal in the mixture, etc., and proper conditions may be selected as necessary.
  • the sintering temperature may vary depending on the type of material used to prepare the porous structure, and is typically set to the level of about 1/2 ⁇ 9/10 of the melting point of the porous structure. Although sintering may occur even in the absence of pressure, sintering may rapidly progress in proportion to an increase in pressure. However, as the pressure is higher, there is a need for additional costs including device cost and mold cost, and thus the appropriate pressure should be selected.
  • a-1) is described below for the case of using a metal and a polymer to prepare the porous structure.
  • the surface of a polymer is plated with a precious metal, such as gold, platinum, and Pd. Subsequently, the polymer is removed, thus obtaining a metal porous structure having better biocompatibility.
  • a precious metal such as gold, platinum, and Pd.
  • a-1 is described below for the case of using an aqueous salt and a metal to prepare the porous structure.
  • an aqueous salt and metal powder are mixed and then formed at high temperature, thus obtaining a preform.
  • the aqueous salt may include one or more selected from the group consisting of NaNO 2 , KNO 2 , NaNO 3 , NaCl, CuCl, KNO 3 , KCl, LiCl, KNO 3 , PbCl 2 , MgCl 2 , CaCl 2 and BaCl 3 .
  • the preform is pressed at a temperature of 2/10 ⁇ 9/10 of the melting point of the metal powder.
  • the metal powder coheres via migration of atoms to form a structure, and the aqueous salt is contained therein, thus obtaining a composite.
  • the composite is immersed in water, only the aqueous salt may dissolve, resulting in a metal porous structure having pores.
  • a metal porous structure may be obtained by completely melting a metal material and then injecting a foaming agent to generate gas.
  • a-1) is described below for the case when a polymer and an electrolyte having metal ions are used to prepare the porous structure.
  • the surface of a porous polymer is plated with a metal using an electrolyte having metal ions.
  • the metal ions are not particularly limited, but one or more selected from the group consisting of Ti, Co, Cr and Zr may be used. Subsequently, the temperature is increased to remove the polymer, thereby obtaining a metal porous structure.
  • fine ceramic grains and a binder polymer are mixed.
  • the resultant mixture is applied on the surface of a backbone structure made of a foaming agent such as polyurethane which is removable, and then dried thus preparing a porous structure.
  • a foaming agent such as polyurethane which is removable
  • the polymer is combusted and removed at a temperature near the combustion temperature of the binder polymer.
  • the remaining ceramic grains are mutually sintered, resulting in a porous structure having mechanical strength.
  • the fine ceramic grains may comprise one or more selected from the group consisting of hydroxyapatite (HA), zirconia and alumina.
  • a-1) may be a modification or combination of the above methods of producing the porous structure, or may be a method of forming a porous structure having different porosities inside and outside by applying it to some of heterogeneous materials.
  • the latter method enables the production of a porous structure the density of the inside of which is high because there are few or no pores and the porosity of the outside of which is high so that the porosity is different at different positions.
  • This method may be employed upon production of an implant that may endure high external stress throughout its entirety while inducing a high rate of bone formation on the surface of the implant.
  • the production of the porous structure as above is only an illustration among a variety of methods of producing a porous structure, and the scope of the present invention is not limited by variations of the methods of producing the porous structure.
  • a-2) may include one selected from the group consisting of immersing the porous structure in a molten Mg solution, allowing a molten Mg solution to flow in the fixed porous structure so that pores are filled therewith, and applying an external pressure of 1 atm or more in the above two cases so that molten Mg is more easily charged in the pores of the porous structure.
  • the porous structure may be heated or a variety of surface contaminants may be removed so that the molten Mg is easily charged in the pores.
  • a-2) may be as follows: Mg is vaporized at high temperature, preferably 700° C. or more, so that Mg vapor is deposited on the surface of the pores while passing through the pores of the porous structure, thus filling the pores of the porous structure with Mg.
  • a-2) may be as follows: an Mg-containing salt is melted in a liquid, after which Mg is adsorbed on the surface of the pores of a porous structure while passing the porous structure through the liquid.
  • only part of pores of the porous structure may be filled with the Mg alloy, instead of all of them being filled therewith.
  • the molten Mg is charged in the porous structure, after which high-pressure gas is blown into the porous structure or the porous structure is rotated or stirred before Mg is completely solidified.
  • non-solidified Mg is removed from the porous structure and only part of Mg may be left behind in the pores, thus obtaining a composite in which part of the pores is impregnated with Mg.
  • a rate of charging Mg may be differently controlled at positions of the pores of the porous structure.
  • the application of Mg is controlled such that Mg is applied only to the surface of the backbone of the porous structure and a predetermined portion of the pores may remain unfilled, and thereby additional effects are expected including it being easier to form bone by Mg while maintaining spaces wherein the fine blood vessels necessary to form bone may be easily formed in the implant.
  • the biodegradable polymer having a polymer and Mg may be manufactured by mixing Mg powder and the polymer at a volume ratio of 5:95 to 95:5, increasing the temperature to 150 ⁇ 500° C. and applying pressure in the range of 1 atm to 100 atm.
  • the above conditions are preferable for the manufacture of the polymer-Mg biodegradable implant, but under conditions falling outside of the above conditions, the polymer-Mg biodegradable implant may also be formed. Thus it will infringe the scope of the present invention to change the manufacturing conditions for manufacturing the polymer-Mg biodegradable implant.
  • the method of manufacturing the porous structure made of metal, ceramic and polymer, the method of filling pores of the porous structure with Mg alloy, and the method of manufacturing the Mg-filled polymer biodegradable implant are merely illustrative in the present invention, and the scope of the present invention is not limited thereto.
  • b) may be forming the molten Mg alloy for controlling a biodegradation rate using one or more selected from the group consisting of cooling, extrusion and metal processing.
  • the cooling process may be used to enhance the mechanical strength of the Mg alloy. Specifically, when Mg is melted in a), immersing a crucible including molten Mg in water may be utilized. Also, the molten Mg may be cooled by spraying an inert gas such as argon. The cooling process using spraying is performed at a much higher rate thus obtaining a very fine framework. However, in the case where Mg is cast in a small size, it should be noted that a plurality of pores (black portion) be formed therein.
  • the extrusion process is used to make the framework of the Mg uniform and enhance mechanical performance.
  • the extrusion process may be performed at 300 ⁇ 450° C.
  • the extrusion of Mg may be carried out in a ratio of reduction in the cross-sectional area before and after extrusion (an extrusion ratio) of 10:1 ⁇ 30:1.
  • an extrusion ratio As the extrusion ratio becomes higher, the fine framework of the extrusion material may become uniform, and defects caused upon casting may be easily removed. In this case, it is preferred that the capacity of an extrusion device be increased.
  • molten Mg may be poured onto a mold processed to have a shape close to a shape of a final product and thus directly cast, or may be prepared into an intermediate material such as a rod or a sheet and then subjected to turning or milling, and also the Mg alloy may be forged at a higher pressure thus obtaining a final product.
  • the biodegradable implant according to the present invention comprises an Mg alloy which is represented by Chemical Formula 1 below and comprises based on the total weight thereof, 23 wt % or less but exceeding 0 wt % of Ca, 10 wt % or less but exceeding 0 wt % of X, and a remainder of Mg.
  • X is Mn or Zn.
  • a biodegradable implant in which mechanical properties and corrosion resistance are simultaneously improved and brittleness fractures do not occur may be provided.
  • the Mg alloy preferably comprises, based on the total weight thereof, 23 wt % or less but exceeding 0 wt % of Ca, 0.1 ⁇ 5 wt % of X and the remainder of Mg, and more preferably 23 wt % or less but exceeding 0 wt % of Ca, 0.1 ⁇ 3 wt % of X and the remainder of Mg.
  • the same corrosion rate is embodied, the case where the amount of impurities is low is favorable for fear of the impurities causing side effects.
  • a biodegradable implant obtained by filling pores of a porous structure with the Mg alloy represented by Chemical Formula 1, comprising, based on the total weight thereof, less than 23 wt % but exceeding 0 wt % of Ca, less than 10 wt % but exceeding 0 wt % of X, and a remainder of Mg.
  • the size of pores of the porous structure is preferably 200 ⁇ 500 ⁇ m.
  • the pore size may be adjusted depending on the application field using typical methods of the art. When the pore size falls within the above range, it is easy to allow blood vessels responsible for supplying nutrients, minerals and ions to pass through the pores.
  • the porous structure may have a porosity of 5 ⁇ 95%.
  • the porosity is a volume ratio of pores relative to total volume. In the case where the required strength of a target is high, the porosity is decreased so that the strength of the porous structure may be increased.
  • the porous structure is a metal such as tantalum having high strength or merely functions to fill the cavities of lost bone, high porosity thereof does not cause problems.
  • the porous structure may be formed of one or more selected from the group consisting of a metal, a ceramic and a polymer.
  • the metal may include one or more selected from the group consisting of titanium or a titanium alloy, a cobalt-chromium alloy and stainless steel.
  • the ceramic may include one or more selected from the group consisting of calcium phosphate, alumina, zirconia and magnesia.
  • the polymer may include one or more selected from the group consisting of polyethylene, polylactic acids (PLA), polyglycolic acid (PGA) and a copolymer thereof such as PLGA. In the case where the porous structure is made with the above polymer, a biodegradable acid may be produced thus decreasing the pH.
  • Mg may increase the pH while it is decomposing, and thus an additional effect of arbitrarily adjusting the pH in vivo via control of the rate of decomposition of the polymer and Mg may be expected.
  • the biodegradable implant according to the present invention may be used for orthopedics, dental care, plastic surgery or blood vessels.
  • the above implant may be utilized for an interbody spacer for the spine, a bone filler, a bone plate, bone pin, bone screw, scaffold, and artificial dental root.
  • the biodegradable implant according to the present invention is manufactured by i) providing an Mg alloy represented by Chemical Formula 1 below, comprising based on the total weight thereof less than 23 wt % but exceeding 0 wt % of Ca, less than 10 wt % but exceeding 0 wt % of X, and less than 100 wt % but exceeding 67 wt % of Mg; and ii) forming the Mg alloy.
  • an Mg alloy represented by Chemical Formula 1 below comprising based on the total weight thereof less than 23 wt % but exceeding 0 wt % of Ca, less than 10 wt % but exceeding 0 wt % of X, and less than 100 wt % but exceeding 67 wt % of Mg.
  • X is Mn or Zn.
  • i) is preferably providing the Mg alloy in a molten state.
  • the description of i) is the same as that of a) and is thus omitted.
  • i) may comprise i-1) preparing a porous structure and i-2) filling the pores of the porous structure with the Mg alloy.
  • i-1) and i-2) are the same as that of a-1) and a-2) and is thus omitted.
  • the method of manufacturing the biodegradable implant according to the present invention may be forming the molten Mg alloy for controlling a biodegradation rate using one or more selected from the group consisting of cooling, extrusion and metal processing.
  • the present invention provides a method of manufacturing a biodegradable implant, comprising applying ultrasound to the biodegradable implant comprising Mg.
  • ultrasound is applied to the biodegradable implant comprising Mg, the corrosion rate may increase in vivo, so that the implant may disappear within a shorter period of time.
  • the biodegradable implant comprising Mg may be a porous structure, wherein Mg contains as impurities (i) Mn and (ii) one selected from the group consisting of Fe, Ni and mixtures of Fe and Ni, wherein the impurities satisfy the following condition: 0 ⁇ (ii)/(i) ⁇ 5, and an amount of the impurities is 1 part by weight or less but exceeding 0 parts by weight based on 100 parts by weight of the magnesium.
  • the biodegradable implant may include an Mg alloy represented by Chemical Formula 1 below, comprising based on the total weight thereof, less than 23 wt % but exceeding 0 wt % of Ca, less than 10 wt % but exceeding 0 wt % of X, and less than 100 wt % but exceeding 67 wt % of Mg.
  • Chemical Formula 1 an Mg alloy represented by Chemical Formula 1 below, comprising based on the total weight thereof, less than 23 wt % but exceeding 0 wt % of Ca, less than 10 wt % but exceeding 0 wt % of X, and less than 100 wt % but exceeding 67 wt % of Mg.
  • X is Mn or Zn.
  • the biodegradable implant according to the present invention may be advantageously present in vivo for a long period of time because the biodegradation rate is controlled to be very low. Also, in the case where the biodegradable implant according to the present invention includes a porous structure, blood vessels that pass through the pores are formed, thus increasing the rate at which bone is formed and decreasing Young's modulus to thereby reduce stress shielding. Also, the biodegradable implant according to the present invention may have enhanced mechanical strength and impact resistance. Also, the biodegradable implant according to the present invention may be simultaneously improved in terms of corrosion resistance and mechanical properties. Thus, the implant according to the present invention is adapted to be used in bone replacements or treatment for bone and may be used for orthopedics, dental care, plastic surgery or blood vessels.
  • the biodegradable implant according to the present invention comprises, based on the total weight thereof, 10 wt % or less but exceeding 0 wt % of Mn; 1 wt % or less but exceeding 0 wt % of Fe; and 99 wt % to less than 100 wt % of a metal comprising Mg.
  • the Mn content may be set to 0.3 ⁇ 0.6 wt %.
  • Fe is further included as an impurity.
  • the biodegradable implant according to the present invention includes Mn in the above content range, which is bound with Fe contained in the metal comprising Mg thus decreasing a difference in potential to thereby reduce galvanic corrosion. Furthermore, Fe contained in the metal comprising Mg is enclosed with Mn so that contact between Mg and Fe is blocked, thus preventing or reducing the corrosion.
  • the metal comprising Mg may be pure Mg, Mg having a very small amount of impurity, or an Mg alloy.
  • This impurity X may be selected from the group consisting of zirconium (Zr), molybdenum (Mo), niobium (Nb), tantalum (Ta), titanium (Ti), strontium (Sr), chromium (Cr), manganese (Mn), zinc (Zn), silicon (Si), phosphorus (P) and nickel (Ni).
  • the biodegradable implant according to the present invention comprises, based on the total weight thereof, 90 wt % or less but exceeding 0 wt % of magnesium oxide (MgO); and 10 wt % to less than 100 wt % of a metal comprising Mg.
  • MgO magnesium oxide
  • the corrosion properties of the biodegradable implant are controlled, thus preventing swelling due to hydrogen being generated upon insertion of the biodegradable implant in vivo.
  • the corrosion of the metal comprising Mg may be reduced.
  • MgO be contained in the above amount range.
  • the metal comprising Mg may be pure Mg, Mg having a very small amount of impurity, or an Mg alloy.
  • This impurity X may be selected from the group consisting of zirconium (Zr), molybdenum (Mo), niobium (Nb), tantalum (Ta), titanium (Ti), strontium (Sr), chromium (Cr), manganese (Mn), zinc (Zn), silicon (Si), phosphorus (P) and nickel (Ni).
  • the biodegradable implant according to the present invention may prevent PCP (Preferred Crystallographic Pitting Corrosion) caused by coarse crystal grains therein, using extrusion. Specifically, when crystal grains are coarse, the probability of corrosion between the crystal grains is high. The size of crystal grains is decreased via extrusion so that the intervals between crystal grains are decreased, thereby preventing such corrosion.
  • PCP Preferred Crystallographic Pitting Corrosion
  • the ratio of reduction in the cross-sectional area before and after extrusion is not particularly limited so long as it is 2:1 or more, but preferably exceeds 25:1 or 20:1.
  • Biodegradable Implant comprising Mg Alloy for Controlling Biodegradation Rate comprising 1 part by weight or less but exceeding 0 parts by weight of Total of Impurities including Mn, Fe and Ni based on 100 parts by weight of Mg and the impurities satisfying the following condition: 0 ⁇ Fe+Ni ⁇ /Mn ⁇ 5
  • Fe, Ni, Al, Mn and Mg in the amounts shown in Table 1 below were charged in a crucible having an inner diameter of 50 mm made of stainless steel (SUS 410). Subsequently, while Ar gas was allowed to flow around the crucible so that Fe, Ni, Mn, Al and Mg in the crucible did not come into contact with air, the temperature of the crucible was increased to about 700 ⁇ 750° C. inside a resistance heating furnace so that the Fe, Ni, Al, Mn and Mg melted. The crucible was stirred so that the molten Fe, Ni, Al, Mn and Mg were well mixed. The completely molten Mg alloy was cooled, thus preparing an Mg alloy in the solid phase. Also upon cooling, the crucible was immersed in water to enhance the mechanical strength of Mg, whereby the molten Mg alloy was rapidly cooled.
  • SUS 410 stainless steel
  • the Mg alloy in the solid phase was extruded at 400° C. under conditions of the ratio of reduction in the cross-sectional area before and after extrusion (the extrusion ratio) being set to 15:1.
  • the biodegradable implants of Examples 1 and 2 and Comparative Example 1 were immersed in a solution having a composition of Table 2 below, and thus the corrosion rate was evaluated based on the hydrogen evolution amount in relation to the immersion time. The results are shown in FIG. 1 .
  • Example 1 hydrogen began to occur after 50 hours, and in Example 2, hydrogen was not almost generated from initial immersion to after 200 hours, and thus the implant was slightly corroded. However, in Comparative Example 1, hydrogen was generated from initial immersion. Hence, the biodegradation rate of the biodegradable implants of Examples 1 and 2 satisfying the following condition: 0 ⁇ Fe+Ni ⁇ /Mn ⁇ 5 was slower than that of Comparative Example 1 satisfying the following condition: ⁇ Fe+Ni ⁇ /Mn>5
  • Mg, Ca, Mn and Zn in the amounts shown in Table 3 below were charged in a crucible having an inner diameter of 50 mm made of stainless steel (SUS 410). Subsequently, while Ar gas was allowed to flow around the crucible so that Mg, Ca, Mn and Zn in the crucible did not come into contact with air, the temperature of the crucible was increased to about 700 ⁇ 750° C. inside a resistance heating furnace so that the Mg, Ca, and Mn melted. The crucible was stirred so that the molten Mg, Ca, and Mn were well mixed. The completely molten Mg alloy was cooled, thus preparing an Mg alloy in the solid phase. Also upon cooling, the crucible was immersed in water to enhance the mechanical strength of Mg, whereby the molten Mg alloy was rapidly cooled.
  • SUS 410 stainless steel
  • the Mg alloy in the solid phase was extruded at 400° C. under conditions of the ratio of reduction in the cross-sectional area before and after extrusion (the extrusion ratio) being set to 15:1.
  • FIG. 2 shows results of evaluating mechanical strength of the biodegradable implant before extrusion
  • FIG. 3 shows results of evaluating mechanical strength of the biodegradable implant before extrusion.
  • Example 3 before extrusion, Example 3 had a yield strength of 180 Mpa, which was slightly lower than 220 MPa of Comparative Example 3, and also after extrusion, Example 3 had 280 MPa which was slightly lower than 320 MPa of Comparative Example 3. However, because 280 MPa is a value that is sufficiently applicable to implant products that undergo loads, the corresponding implant may be reasonably applied to products. Also, the elongation did not reach 7 ⁇ 10% before extrusion and was increased to 12 ⁇ 16% after extrusion. This means that performance in terms of enduring a strong external impact is superior.
  • Example 4 had a strength of 170 Mpa which was lower than 220 MPa, but maintained 320 Mpa equal to that of Comparative Example 3 after extrusion. The elongation was increased from 12% before extrusion to 17% after extrusion and thus mechanical properties were equal to or better than those of Comparative Example 3.
  • the yield strength refers to the strength at the point in time at which the gradient changes in each graph.
  • the biodegradable implants of Examples 3 to 11 and Comparative Examples 3 to 6 were immersed in a biomimetic solution having a composition of Table 2, and thus the corrosion rate was evaluated based on the hydrogen evolution rate in relation to the immersion time. This is because the corrosion rate of an implant is typically determined from the hydrogen evolution rate in the biomimetic solution because hydrogen is generated upon the biodegradation of Mg.
  • FIG. 4 is a graph showing the hydrogen evolution rate in relation to the immersion time in Examples 3 and 4 and Comparative Example 3.
  • FIG. 5 is a graph showing the hydrogen evolution rate in relation to the immersion time in Examples 4 to 6 before extrusion.
  • FIG. 6 is a graph showing the hydrogen evolution amount in relation to the immersion time in Examples 7 to 11 and Comparative Examples 2 and 4 before extrusion.
  • FIG. 7 is a graph showing the hydrogen evolution amount in relation to the Zn content.
  • Example 3 rapid decomposition began to occur after 5 hours, but in Example 3 rapid decomposition began to occur after 17 hours. In Example 4, 30 days after immersion, drastic corrosion did not take place.
  • the biodegradable implants according to the present invention exhibited superior corrosion resistance compared to Comparative Example 3.
  • the corrosion rate was increased in proportion to an increase in the Zn content.
  • the corrosion rate in relation to the Zn content was represented when the hydrogen evolution amount was 0.5 ml/cm'.
  • the optimal composition of the present alloy was 0.1 ⁇ 5% and preferably 0.1 ⁇ 3%. The reason is that the corrosion rate zone is the same, but the low Zn content is regarded as good on the assumption of the same corrosion rate in light of the side effects that Zn has on the human body.
  • Example 7 On the axis x, 0.5 designates Example 7, 0.76 designates Example 8, 1.63 designates Example 9, 3 designates Example 10, and 4.12 designates Example 11.
  • FIG. 8 is an electron microscope image showing the surface of the implant sample of Example 7 immersed in the biomimetic solution for 61 hours
  • FIG. 9 is an EDS image showing the surface of the implant sample of Example 7.
  • FIG. 10 is an image showing the implant sample of Example 7 from which the corrosion material was removed.
  • the corrosion material was produced on the surface.
  • the components of the corrosion material are given in Table 4 below.
  • FIG. 10 shows the implant sample from which the corrosion material shown in FIGS. 8 and 9 was removed.
  • the results of analyzing the implant sample of Example 7 having no corrosion material are shown in Table 5 below.
  • FIG. 11 is an image showing the cross-section of the implant sample of Example 7 immersed in the biomimetic solution for 61 hours
  • FIG. 12 is an enlarged image of the image of FIG. 11
  • FIG. 13 is of WDS (JXA-8500F, available from JEOL) images showing the implant sample of Example 7 immersed in the biomimetic solution of Table 2 for 61 hours.
  • the bright line region in Mg designates Mg 2 Ca
  • the dark line region designates a corroded portion. The corrosion was observed to progress while the black line gradually penetrated in Mg.
  • FIG. 14 is an image showing the cross-section of the implant sample of Example 8 immersed in the biomimetic solution for 61 hours.
  • FIG. 15 is of WDS (JXA-8500F, available from JEOL) images showing the implant sample of Example 8 immersed in the biomimetic solution for 61 hours.
  • M Ca(Zn) was enclosed with the Mg—Ca—Zn compound.
  • Zn was further contained in Mg 2 Ca.
  • the implant sample of Example 8 was cut to a width of 9.65 cm, a length of 19.66 cm, and a thickness of 1.18 cm, thus preparing two samples. Ultrasound was applied to two samples, and then the samples were immersed in the biomimetic solution of Table 2 for 3 hours and the hydrogen evolution amount was measured. The results are shown in FIGS. 15 and 16 .
  • the sample to which ultrasound was applied generated a large amount of hydrogen, and thus was more quickly corroded.
  • Mg and Mn in the amounts shown in Table 7 below were charged in a crucible having an inner diameter of 50 mm that was made of stainless steel (SUS 410). Subsequently, while Ar gas was allowed to flow around the crucible so that Mg and Mn in the crucible did not come into contact with air, the temperature of the crucible was increased to about 700 ⁇ 750° C. inside a resistance heating furnace, so that the Mg and Mn melted. The crucible was stirred so that the molten Mg and Mn were well mixed. The completely molten Mg alloy was cooled, thus preparing an Mg alloy in the solid phase. Also upon cooling, the crucible was immersed in water to enhance the mechanical strength of Mg, whereby the molten Mg alloy was rapidly cooled, resulting in a biodegradable implant
  • the implant samples of Examples 12 to 14 were cut to a width of 9.65 cm, a length of 19.66 cm, and a thickness of 1.18 cm, thus preparing two samples. Ultrasound was applied to the two samples, after which the samples were immersed in the biomimetic solution of Table 2 for 3 hours, and the hydrogen evolution amount was measured. The results are shown in FIG. 18 .
  • the biodegradable implant of Example 14 was extruded at 400° C., and the ratio of reduction in the cross-sectional area before and after extrusion (the extrusion ratio) was set to 25:1.
  • the biodegradable implant of Example 14 before and after extrusion was immersed in the biomimetic solution of Table 2 for 3 hours and the hydrogen evolution amount was measured.
  • FIG. 19 is of images showing the crystal grains when the biodegradable implant of Example 14 was not extruded.
  • FIG. 20 is a graph showing corrosion properties of the biodegradable implant of Example 14 before and after extrusion.
  • Mg and MgO in the amounts shown in Table 8 below were charged in a crucible having an inner diameter of 50 mm made of stainless steel (SUS 410). Subsequently, while Ar gas was allowed to flow around the crucible so that Mg and MgO in the crucible did not come into contact with air, the temperature of the crucible was increased to about 700 ⁇ 750° C. inside a resistance heating furnace, so that the Mg and MgO melted. The crucible was stirred so that the molten Mg and MgO were well mixed. The completely molten Mg alloy was cooled, thus preparing an Mg alloy in the solid phase. Also upon cooling, the crucible was immersed in water to enhance the mechanical strength of Mg, whereby the molten Mg alloy was rapidly cooled, resulting in a biodegradable implant
  • Example 15 The biodegradable implant samples of Example 15 and Comparative Example 4 were inserted into a rat to evaluate the hydrogen evolution amount in vivo.
  • FIG. 21 is a photograph showing the rat having the biodegradable implant sample of Comparative Example 4 inserted therein.

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US20160000964A1 (en) 2016-01-07

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