• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:

    公开号:AT510087A1
    申请号:T0113410
    申请日:2010-07-06
    公开日:2012-01-15
    发明作者:Andreas Dr Schiffl；Bernhard Dr Mingler
    申请人:Ait Austrian Inst Technology；
    IPC主号:
    专利说明:

    1
    magnesium alloy
    The invention relates to a magnesium alloy and its use and an implant of a magnesium alloy. 5
    Furthermore, the invention relates to a method for producing a body, in particular an implant, from a magnesium alloy.
    In implant technology, magnesium alloy implants 10 are currently being studied extensively as biodegradable medical products used in the human or animal body. The background to this is that implants made of magnesium alloys, depending on the nature of the respective alloy, are dissolvable by body fluids. It follows that bone or intramedullary nails or other implants made of a biodegradable magnesium alloy in a human or animal body can be used and then, preferably, only after fulfilling a medical function, dissolve readily. This is a significant advantage over conventional implants because no further surgery is required to remove an implant from the body after performing a medical or therapeutic function. Ideally, the implant should remain stable for as long as a medical or therapeutic function is desired and immediately thereafter dissolve completely under the action of a body fluid.
    In particular, magnesium-zinc alloys 25 are considered in this context, since magnesium-zinc alloys have high strength values, which is necessary or at least necessary for the fulfillment of a medical or therapeutic function.
    In order to achieve a minimum required strength for certain applications, magnesium-zinc alloys are often used in other areas as well. With such alloys, although high-strength bodies can be produced, in particular at higher zinc contents, the inventors have recognized that there is often a high tendency to crack in the production of the bodies (so-called "hot tearing"). However, a hot cracking tendency can cause a cast bolt in the
    • «« • · «« * «· *« «« • · B · * | I * * »·« · ··
    • I ··· I »# * k * * I *« «« «« · · 2
    Surface area, depending on a required quality, must be machined to obtain for further processing, in particular a production of end products, flawless material. This requires a further process step, which not only brings additional time and effort, but also leads to a considerable waste of material. However, a hot crack tendency can also go so far that hot cracks in the middle of a casting are present, resulting in the same. For example, a bolt can no longer be crimped if there is a crack in the center of the bolt. 10 object of the invention is to provide an alloy of the type mentioned, in which a warm crack tendency is reduced.
    Another object of the invention is to illustrate a use of such an alloy. 15
    Further, it is an object of the invention to provide an implant which can be manufactured cost-effectively.
    Finally, it is an object of the invention to provide a method of the aforementioned type 20, with which a body of a magnesium alloy can be produced without or at least with a reduced number of hot cracks.
    The above object is achieved according to the invention by a magnesium alloy containing (in weight percent) 25 more than 0.0 up to 7.0% zinc optionally more than 0.0 up to 1.0% zirconium optionally more than 0.0 up to 1.0% calcium optional more than 0.0 up to 1.0% manganese optional more than 0.0 up to 0.5% silicon 30 optional more than 0.0 up to 1.0% silver maximum up to 0, 5% aluminum and at least one element selected from the group consisting of more than 0.05 up to 0.6% yttrium 3 more than 0.05 up to 4.0% ytterbium more than 0.05 up to 4.0% gadolinium
    Remaining magnesium and production-related impurities.
    In the context of the invention, it has been recognized that even low yttrium and / or ytterbium and / or gadolinium contents in the case of a magnesium-zinc alloy lead to a marked reduction in a hot cracking tendency of the magnesium alloy. This can be justified by the fact that intermetallic phases are formed by the addition of corresponding elements in the production of a melt, whereby a solidus line is raised and a solidification interval is reduced and thus a thermal shrinkage responsible for a hot cracking tendency is reduced. At the same time this results in a subsequent thermal treatment, in particular an extrusion, extruding or rolling a larger thermal window, since the magnesium alloy can be treated without partial melting at much higher temperatures than previously known alloys of this type.
    A magnesium alloy according to the invention contains zinc, so that high mechanical properties are obtained, which may be necessary for various applications such as stents. It is preferably provided that the magnesium alloy contains 1.0 to 5.0%, preferably 2.5 to 4.5%, of zinc. An alloy of the invention may be relatively high levels of zinc of z. B. contain more than 2.5%, which gives a desired high strength, without a practically significant hot crack tendency would be given.
    Furthermore, a magnesium alloy according to the invention may contain zirconium and / or calcium up to 1.0% each, for the purposes of grain refining. It is preferably provided that the magnesium alloy contains more than 0.1 to 0.6%.
    Zirconium and / or more than 0.1 to 0.4% calcium.
    In principle, zirconium and calcium may also be constituents of intermetallic phases which are formed during the production of the magnesium alloy or cooling of a melt corresponding to the composition. The formation of desired ternary intermetallic phases with the elements yttrium, ytterbium and / or gadolinium.... 4... On the one hand not to prevent, but on the other hand also to ensure a desired Kornfeinung, a sum of zirconium and calcium is advantageously 0.6 to 1.0%. Furthermore, a magnesium alloy according to the invention may comprise manganese, silicon and / or silver with the abovementioned maximum contents. In particular, it may be provided that the magnesium alloy comprises at least one element selected from the group consisting of more than 0.1 to 0.5% manganese 10 contains more than 0.1 to 0.5% silicon more than 0.1 to 0.5% silver. Silver and silicon contribute to a fine grain of a structure of the magnesium alloy. Manganese improves corrosion resistance of the magnesium alloy. 15
    Levels of the elements yttrium, ytterbium and / or gadolinium are preferably adjusted so that the magnesium alloy contains at least one element selected from the group consisting of more than 0.05 to less than 0.5% yttrium 20 more than 0.1 to 1, 2% ytterbium contains more than 0.1 to 1.2% gadolinium. This is due to the fact that ytterbium and gadolinium have approximately twice the atomic mass in comparison to yttrium. Thus, if the elements mentioned are present individually, a double amount of ytterbium or gadolinium must be provided relative to yttrium in order to obtain intermetallic phases which act analogously. The stated lower limits of 0.05% for yttrium and 0.1% for ytterbium and gadolinium, respectively, represent minimum contents which are required with regard to the formation of intermetallic phases. It is preferable that a lower limit is set to be 0.1% for yttrium and 0.2% each for ytterbium and gadolinium. Maximum contents of 0.5% for yttrium and 1.2% each for ytterbium and gadolinium may be appropriate to prevent a hot cracking tendency, but also to minimize the cytotoxicity of implants. In particular, it may also be provided that a plurality of the elements named "" "<-> * * * *" "I" · Φ · «« «» »» · · · · · I I I I I I * * * * * * * * * * · I «·
    ··· * · I • · · * * φ · * * ·· * · φ 5 are present at the same time, whereby a maximum sum content is less than 2.5%.
    An aluminum content is limited to a maximum of up to 0.5% because aluminum can mask the beneficial effects of yttrium, ytterbium and / or gadolinium.
    A magnesium alloy according to the invention can be used in all areas in which a low tendency to crack cracks is desired, for example in the production of components for motor vehicles made of high-strength magnesium alloys with a zinc content of more than 2.5%. Preferably, however, it is provided that a magnesium alloy according to the invention is used for producing a biodegradable implant, in particular for use in a medullary cavity of a human body.
    The further object of the invention is achieved when a method of the aforementioned
    The method comprises the following steps: a) preparation of a melt containing more than 0.0 up to 7.0% zinc optionally more than 0.0 up to 1.0% zirconium optionally more than 0.0 up to 1.0% calcium optionally more than 0.0 up to 1.0% manganese optionally more than 0.0 up to 0.5% silicon optionally more than 0.0 up to 1.0% silver maximum up to 0.5% aluminum and at least one Element selected from the group consisting of more than 0.05 up to 0.6% yttrium more than 0.05 up to 4.0% ytterbium more than 0.05 up to 4.0% gadolinium
    Remainder of magnesium and production-related impurities, b) casting the melt into a solid mass, c) annealing the solid mass,
    * * »« * * * · * * * 4 * f * I · · · ** ··· I «(« »» * * «« * • · · · * * · «« · Optionally forming the solid mass or a part thereof, e) producing the body from the optionally formed mass or parts thereof.
    An advantage achieved by the invention is the fact that a body can be produced, 5 has a low tendency to hot crack. As a result, complex and unnecessary waste leading to machining operations such as a machining of a surface of the body can be omitted after production thereof. In addition, a manufactured body is particularly suitable for further processing into medical products, in particular implants for osteosynthesis, for example bone plates, bone screws, intramedullary nails or so-called Kirschner wires. It is advantageous that the magnesium alloy in the body dissolves by itself after a predetermined time due to the action of body fluids. The yttrium, ytterbium and / or gadolinium elements provided during manufacture ensure that a temperature window for a melt solidification is raised relatively small or a solidus line as compared to a magnesium-zinc alloy, leading to the desired reduction in hot cracking tendency as well at zinc levels above 2.5%. The contents of the individual elements yttrium, ytterbium and / or gadolinium are advantageously adjusted so that form during a phase of solidification of the melt due to the 20 distribution coefficients intermetallic phases, which comes under the influence of segregation to an increase in concentration of the element or elements whose activity already early in a solidification interval leads to the precipitation of a ternary intermetallic compound or compounds of the element (s) with magnesium and zinc using the entire residual melt, whereby zinc for a reaction otherwise occurring only at much lower temperatures with formation of a binary metallic Magnesium and zinc compound is no longer or only partially available, which leads to an increase in the solidus line. Furthermore, contents of the elements yttrium, ytterbium and / or gadolinium are adjusted so that when using the magnesium alloy as an implant, the intermetallic phases and the matrix dissolve approximately equally fast so that after dissolution of the implant no unwanted cytotoxic components are present in the body.
    Continuous casting is generally used as the casting method, although low-pressure casting, die-casting, sand casting and chill casting processes can also be used. 7 • * ♦ ♦ • • 4 · • · ·
    Annealing is preferably carried out at an annealing temperature of 280 ° C to 400 ° C. If a reshaping, z. As an extrusion, Equal Channel Angular Pressing (also known as "ECAP") and / or forging, is provided, this is performed below the annealing temperature.
    In a method according to the invention, it may be advantageous to limit the contents of individual elements as stated above in order to achieve the advantages already mentioned.
    Further features, advantages and effects of the invention will become apparent from the embodiments illustrated below. In the drawings, to which reference is made, show:
    Fig. 1 is a diagram relating to a hot crack inclination;
    2 shows a diagram relating to a hot crack tendency as a function of a solidification interval;
    Fig. 3 shows an isothermal section at 300 ° C for magnesium-zinc alloys with different contents of yttrium and gadolinium.
    Magnesium-zinc alloys with various contents of yttrium, ytterbium and / or gadolinium were poured at 700 ° C in a star mold made of a steel. The star-shaped components had elongated rod-shaped areas of 25, 45, 65, 95, 125, and 175 mm in length; a diameter was constant 10 mm. For each magnesium-zinc alloy, five such components were created. The steel star mold was heated to a temperature of 250 ± 5 ° C before pouring. The casting temperature of 700 ° C corresponded to an overheating of the melts of about 60 ° C. After casting, the star mold was allowed to rest for five minutes and then opened to examine the cast-off moldings.
    In the above manner, magnesium-zinc alloys having yttrium contents of up to 0.8% were prepared. The alloys contained, besides magnesium, 3.0% zinc, about 0.4% zirconium, about 0.3% calcium, and optionally 0.15% manganese, 0.4 to 0.8% yttrium, and / or 2.0% ytterbium and / or 2.0% gadolinium. H MM 4 • · • • · · · ·
    The individual components were subsequently examined for cracks, with an evaluation of the quality of the individual segments by means of a visual examination of the elongated regions of the components. The samples were further examined for internal cracks.
    Inside the individual components, no cracks could be detected. With respect to a number of cracks on a surface, magnesium alloys prepared with yttrium showed no or only a small number of hot cracks. With increasing yttrium content, the warm cracks decreased. A similar picture emerged in further experiments, with corresponding melts were not created in star-shaped molds, but in the so-called "direct chill casting" or by continuous casting; the corresponding data are shown in FIG. From Fig. 1 it is clear that a hot crack tendency decreases with increasing yttrium content. However, as the yttrium content in a magnesium alloy increases, so does the risk that an implant of the magnesium alloy will dissolve in the body after a predetermined time, but yttrium will remain. For this reason, when using corresponding magnesium alloys for implants, an yttrium content is limited to a maximum of 0.6%, preferably less than 0.5%. For magnesium alloys in which yttrium was replaced by ytterbium, as well as for magnesium alloys with gadolinium, corresponding results were obtained. In other words: In all cases, a hot crack tendency could be significantly reduced, with the ytterbium and gadolinium contents being twice as high as the yttrium contents. This can be attributed to the fact that intermetallic phases form with the three mentioned elements, whereby due to the atomic masses, the contents of ytterbium and / or gadolinium can be significantly higher than those of yttrium.
    By alloying in yttrium, ytterbium and / or gadolinium, the solidus line of a magnesium-zinc alloy can be raised, resulting in a reduction of the hot cracking tendency of such a magnesium alloy. This is illustrated in FIG. 2. As can be seen, a number of hot cracks decrease with decreasing melt interval, with favorable results already at yttrium contents of less than 0.5%. * * * · # · · · «* * · &Gt; . Fig. 3 is a calculated isothermal section at 300 ° C for magnesium-zinc alloys with 3.0% zinc, 0.3% zirconium and various levels of yttrium and gadolinium. The temperature of 300 ° C corresponds to a typical extrusion temperature. As can be seen, with yttrium contents up to 0.6%, only one yttrium-poor intermetallic phase Mg3YZnB is present, while at higher yttrium contents there is also a yttrium-rich phase MgYZn3. The yttrium-poor phase is considered to be more favorable for biodegradable implants, if an intermetallic phase in the body should dissolve or only very slowly, since a local concentration is then lower. In addition, a better solubility of the yttrium-poor phase is suspected.
    It is also apparent from the isothermal section according to FIG. 3 that gadolinium can be present in addition to yttrium without any change in the nature of the yttrium phases. In particular, high gadolinium contents can also be provided without negative interaction, whereby the solubility of the intermetallic phases does not change.
    Magnesium alloys according to the invention were, as mentioned, also produced by continuous casting, wherein an average grain size of the microstructure as well as in chill casting was less than 50 μm for all magnesium alloys according to the invention. By a subsequent annealing at an annealing temperature of 280 ° C to 400 ° C and then extruding parts of the continuously cast magnesium alloys, a further reduction of the grain size could be achieved. In particular, magnesium alloys with ytterbium, for example a magnesium-zinc alloy with 2% ytterbium, showed both high strength and high elongation at break (yield strength Rp0.2 about 300 MPa, breaking elongation Af about 25%). Magnesium alloys with such favorable property values are not only suitable for the production of biodegradable implants, but can also be used in particular for the production of thermally and / or mechanically stressed components, for example components of motor vehicles that are subject to a high static and / or dynamic load subject.
    权利要求:
    Claims (13)
    [1]
    4 »« «« * * * * ft ·························································································· 1. Magnesium alloy containing (in weight percent) more than 0.0 up to 7.0% zinc optionally more than 0.0 up to 1.0% zirconium optionally more than 0.0 up to 1.0% calcium optional more than 0.0 up to 1.0% manganese optional more than 0.0 up to 0.5% silicon optional more than 0.0 up to 1.0% silver maximum up to 0 , 5% aluminum and at least one element selected from the group consisting of more than 0.05 to 0.6% yttrium more than 0.05 to 4.0% ytterbium more than 0.05 to 4.0% gadolinium Remaining magnesium and production-related impurities.
    [2]
    2. Magnesium alloy according to claim 1, containing 1.0 to 5.0%, preferably 2.5 to 4.5%, zinc.
    [3]
    3. The magnesium alloy according to claim 1 or 2, containing more than 0.1 to 0.6% zirconium and / or more than 0.1 to 0.4% calcium.
    [4]
    The magnesium alloy according to claim 3, wherein a sum content of zirconium and calcium is 0.6 to 1.0%.
    [5]
    5. The magnesium alloy according to any one of claims 1 to 4, containing at least one element selected from the group consisting of more than 0.1 to 0.5% manganese more than 0.1 to 0.5% silicon more than 0.1 up to 0.5% silver. I * * Φ Φ · Φ Φ Φ Φ Φ ΦΦ • «« · · · · · * * * «« ♦ ·· # Φ · · «« · t · · ♦ ♦ # # «· * · · * Φ Φ ··· * · · »» »» »» 11
    [6]
    6. The magnesium alloy according to any one of claims 1 to 5, containing at least one element selected from the group consisting of more than 0.05 to less than 0.5% yttrium more than 0.1 to 1.2% ytterbium more than 0, 1 to 1.2% gadolinium.
    [7]
    7. The magnesium alloy according to any one of claims 1 to 6, containing at least two elements selected from the group consisting of yttrium, ytterbium and gadolinium, wherein a sum amount of these elements is less than 2.5%.
    [8]
    8. Use of a magnesium alloy according to one of claims 1 to 7 for the production of a biodegradable implant, in particular for use in a medullary cavity of a human body.
    [9]
    9. implant of a magnesium alloy according to any one of claims 1 to 7.
    [10]
    10. A process for the production of a body, in particular an implant, from a magnesium alloy, comprising the following steps: a) Preparation of a melt containing more than 0.0 up to 7.0% zinc optionally more than 0.0 up to 1.0 % Zirconium optional more than 0.0 up to 1.0% calcium optional more than 0.0 up to 1.0% manganese optional more than 0.0 up to 0.5% silicon optional more than 0.0 up to 1 , 0% silver maximum up to 0.5% aluminum and at least one element selected from the group consisting of more than 0.05 up to 0.6% yttrium more than 0.05 up to 4.0% ytterbium more than 0, 05 up to 4.0% gadolinium balance magnesium and manufacturing impurities, 12 b) casting the melt into a solid mass, c) annealing the solid mass, d) optionally forming the solid mass or a part thereof, e) producing the body the optionally formed mass or parts thereof. 5
    [11]
    11. The method of claim 10, wherein the annealing is carried out at an annealing temperature of 280 ° C to 400 ° C.
    [12]
    12. The method of claim 10 or 11, wherein a forming is carried out at a temperature 10 below the annealing temperature.
    [13]
    13. The method according to any one of claims 10 to 12, wherein the forming by extrusion, Equal Channel Angular Pressing and / or forging is performed.
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    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JP3415987B2|1996-04-04|2003-06-09|マツダ株式会社|Molding method of heat-resistant magnesium alloy molded member|
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    DE102006015457A1|2006-03-31|2007-10-04|Biotronik Vi Patent Ag|Magnesium alloy and related manufacturing process|
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    GB0813659D0|2008-07-25|2008-09-03|Smith & Nephew|Fracture putty|
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    ATA1134/2010A|AT510087B1|2010-07-06|2010-07-06|MAGNESIUM ALLOY|ATA1134/2010A| AT510087B1|2010-07-06|2010-07-06|MAGNESIUM ALLOY|
    EP11802999.0A| EP2591132B1|2010-07-06|2011-06-15|Magnesium alloy|
    US13/700,858| US9775647B2|2010-07-06|2011-06-15|Magnesium alloy|
    PCT/AT2011/050001| WO2012003522A2|2010-07-06|2011-06-15|Magnesium alloy|
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