This patent application relates to a magnesium alloy and to a method for the production thereof and to the use thereof.

It is known that the properties of magnesium alloys are decisively defined by the type and quantity of the alloying elements and impurities as well as the production conditions. The effects of the alloying elements and impurities on the properties of the magnesium alloys have been known for a long time to a person skilled in the art and illustrate the complex nature of determining the properties of binary or ternary magnesium alloys for the use thereof as implant materials.

The alloying element used most frequently for magnesium is aluminum, resulting in increased tensile strength due to solid solution and precipitation hardening and fine grain formation, but also in microporosity. Moreover, in the melt aluminum shifts the iron precipitation boundary toward drastically lower iron contents at which the iron particles precipitate or form intermetallic particles together with other elements.

Undesirable accompanying elements in magnesium alloys include iron, nickel, cobalt and copper, which cause a considerable increase in the corrosion tendency due to the electropositive nature thereof.

Manganese can be found in all magnesium casting alloys and binds iron in the form of AlMnFe precipitations, whereby the formation of local elements is reduced. On the other hand, manganese is not able to bind all the iron, and therefore a remainder of iron and a remainder of manganese are always left in the melt. Silicon lowers the castability and viscosity, and as the content of Si rises, a worsened corrosion behavior is to be expected. Iron, manganese and silicon have a very high tendency to form an intermetallic phase.

The electrochemical potential of this phase is very high and can thus act as a cathode controlling the corrosion of the alloy matrix.

As a result of solid solution hardening, zinc improves the mechanical properties and results in grain refining, however it also leads to microporosity with a tendency toward hot cracking starting at a content of 1.5 to 2% by weight in binary Mg-Zn and ternary Mg-Al-Zn alloys.

Alloying additions made of zirconium increase the tensile strength without lowering the expansion and lead to grain refining, but also to a strong impairment of dynamic restrystallization, which is manifested in an increase of the recrystallization temperature and therefore requires high energy expenditure. Moreover, zirconium cannot be added to melts containing aluminum and silicon because the grain refining effect is lost.

Rare earths such as Lu, Er, Ho, Th, Sc and In all exhibit a similar chemical behavior and form eutectic systems with partial solubility on the magnesium-rich side of the binary phase diagrams such that precipitation hardening is possible.

The addition of further alloying elements, in conjunction with the impurities, is known to cause the formation of different intermetallic phases in binary magnesium alloys. For example, the intermetallic phase Mg ₁₇ Al ₁₂ forming on the grain boundaries is brittle and limits the ductility. As compared to the magnesium matrix, this intermetallic phase is more noble and able to form local elements, whereby the corrosion behavior worsens.

In addition to these influencing factors, the properties of the magnesium alloys also decisively depend on the metallurgical production conditions. Conventional casting methods automatically introduce impurities when adding, by alloying, the alloying elements. The prior art (US 5,055,254 A) therefore defines tolerance limits for impurities in magnesium casting alloys, which, for example for a magnesium-aluminum-zinc alloy containing approximately 8 to 9.5% by weight Al and 0.45 to 0.9% by weight Zn, mentions tolerance limits of 0.0015 to 0.0024% by weight Fe, 0.0010% Ni, 0.0010 to 0.0024% by weight Cu and no less than 0.15 to 0.5% by weight Mn. Tolerance limits for impurities in magnesium and the alloys thereof as well

as the production conditions are mentioned in many known documents and

listed as follows in % by weight:

It has been found that these tolerance definitions are not sufficient to reliably exclude the formation of corrosion-promoting intermetallic phases, which in terms of electrochemistry have a more noble potential than the magnesium matrix.

Biodegradable implants (orthopedics, traumatology, cardiovascular implants) require a load-bearing function and consequently strength, together with sufficient expandability, during the physiologically necessary support periods thereof. However, especially in this respect, the known magnesium materials cannot come even close to the properties achieved by permanent implants such as titanium, CoCr alloys and titanium alloys. The ultimate tensile strength R _m for permanent implants is approximately 500 MPa to >1000 MPa, while that of magnesium materials is <275 MPa so far, and in most cases <250 MPa.

Another drawback of many technical magnesium materials is that the difference thereof between ultimate tensile strength R _m and proof stress R _p is only small. In the case of implants that allow plastic deformation, such as cardiovascular stents, this means that no further resistance exists against deformation after initial deformation of the material, and the regions that have already been deformed are deformed further without any load increase, whereby overstretching of parts of the component may be caused and fracture may occur.

Many magnesium materials, such as the alloys containing 3 to 10% by weight Al and less than 1% by weight Zn and Mn (AZ group), for example, additionally exhibit a clearly pronounced mechanical asymmetry, which is manifested in the difference in the mechanical properties, especially the proof stress R _p with tension load and compression load. Such asymmetries are created, for example, during forming processes such as extrusion, rolling and drawing, which are used to produce suitable semi-finished products. A difference between the proof stress R _p during tension and the proof stress R _p during compression that is too large may result in inhomogeneous deformation of a component, such as a cardiovascular stent, which later undergoes multiaxial deformation, and may cause cracking and fracture.

Because of the low number of crystallographic slip systems, magnesium alloys can generally also form textures during forming processes such as extrusion, rolling and drawing used to produce suitable semifinished products by orienting the grains during the forming process. Specifically, this means that the semifinished product has different properties in different directions in space. For example, high deformability or elongation at fracture occurs in one direction in space after forming, and reduced deformability or elongation at fracture occurs in another direction in space. The formation of such textures should likewise be avoided, because a stent is subjected to high plastic deformation, and reduced elongation at fracture increases the risk of failure of the implant. One method for substantially avoiding such textures during forming is to adjust as fine a grain as possible prior to forming. Because of the hexagonal lattice structure of magnesium materials, the ability of these materials to deform at room temperature is low, which is characterized by slip in the base plane. If the material additionally has a coarse microstructure, which is to say a coarse grain, so-called twinning is forcibly produced upon further deformation, at which shear strain occurs, which transforms a crystal region into a position that is mirror symmetrical to the starting position. The resulting twin grain boundaries constitute weak points in the material, where incipient cracking starts, especially with plastic deformation, which ultimately leads to the destruction of the component.

If the grain of the implant materials is sufficiently fine, the risk of such implant failure is drastically reduced. Implant materials should therefore have as fine a grain as possible so as to prevent such undesirable shear strain.

All available technical magnesium materials for implants are subject to high corrosion in physiological media. Attempts have been made in the prior art to curb the corrosion tendency by providing the implants with a corrosion-inhibiting coating, for example made of polymeric materials (EP 2 085 100 A2, EP 2 384 725 Al), an aqueous or alcoholic conversion solution (DE 10 2006 060 501 Al) or an oxide (DE 10 2010 027 532 Al, EP 0 295 397 Al).

The use of polymeric passivation layers is highly contested, because virtually all appropriate polymers also cause strong inflammations in the tissue at times. Thin structures without such protective measures do not reach the required support periods. The corrosion on thin-walled traumato logical implants is often times accompanied by an excessively fast loss of tensile strength, which poses an additional burden by forming excessive amounts of hydrogen per unit of time. The consequences are undesirable gas inclusions in the bones and tissue.

In the case of traumato logical implants having larger cross-sections, there is a need to be able to deliberately control the hydrogen problem and the corrosion rate of the implant by way of the structure thereof.

Specifically with biodegradable implants, there is a desire for maximum biocompatibility of the elements, because all the chemical elements that are contained are absorbed by the body after decomposition. In any case, highly toxic elements such as Be, Cd, Pb, Cr and the like should be avoided.

Degradable magnesium alloys are especially suitable for implementing implants which have been employed in a wide variety of forms in modern medical technology. Implants are used, for example, to support vessels, hollow organs and vein systems (endovascular implants, such as stents), for fastening and temporarily fixing tissue implants and tissue transplantations, but also for orthopedic purposes, such as nails, plates or screws. A particularly frequently used form of an implant is the stent.

The implantation of stents has become established as one of the most effective therapeutic measures for the treatment of vascular diseases. Stents have the purpose of assuming a supporting function in hollow organs of a patient. For this purpose, stents featuring conventional designs have a filigree supporting structure comprising metal struts, which is initially present in compressed form for introduction into the body and is expanded at the site of the application. One of the main application areas of such stents is to permanently or temporarily widen and hold open vascular constrictions, particularly constrictions (stenosis) of coronary blood vessels. In addition, aneurysm stents are known, which are used primarily to seal the aneurysm. The support function is additionally provided.

The implant, notably the stent, has a base body made of an implant material. An implant material is a non-living material, which is employed for applications in medicine and interacts with biological systems. A basic prerequisite for the use of a material as an implant material, which is in contact with the body environment when used as intended, is the body friendliness thereof (biocompatibility). For the purpose of the present application, biocompatibility shall be understood to mean the ability of a material to induce an appropriate tissue reaction in a specific application. This includes an adaptation of the chemical, physical, biological, and morphological surface properties of an implant to the recipient's tissue with the aim of a clinically desired interaction. The biocompatibility of the implant material is also dependent on the temporal process of the reaction of the biosystem in which it is implanted. For example, irritations and inflammations occur in a relatively short time, which can lead to tissue changes. Depending on the properties of the implant material, biological systems thus react in different ways. According to the reaction of the biosystem, the implant materials can be divided into bioactive, bioinert and degradable or resorbable materials. Implant materials comprise polymers, metallic materials, and ceramic materials (as coatings, for example). Biocompatible metals and metal alloys for permanent implants comprise, for example, stainless steels (such as 316L), cobalt-based alloys (such as CoCrMo cast alloys, CoCrMo forge alloys, CoCrWNi forge alloys and CoCrNiMo forge alloys), technical pure titanium and titanium alloys (such as cp titanium, TiA16V4 or TiA16Nb7) and gold alloys. In the field of biocorrodible stents, the use of magnesium or technical pure iron as well as biocorrodible base alloys of the elements magnesium, iron, zinc, molybdenum, and tungsten are proposed.

The use of biocorrodible magnesium alloys for temporary implants having filigree structures is made difficult in particular in that the degradation of the implant progresses very quickly in vivo. So as to reduce the corrosion rate, this being the degradation speed, different approaches are being discussed. For one, it is attempted to slow the degradation on the part of the implant material by developing appropriate alloys. In addition, coatings are to bring about a temporary inhibition of the degradation. While the existing approaches are promising, none of them has so far led to a commercially available product. Regardless of the efforts made so far, there is rather a continuing need for solutions that make it possible to at least temporarily reduce the corrosion of magnesium alloys in vivo, while optimizing the mechanical properties thereof at the same time.

In light of this prior art, the objects of the invention are that of providing a biodegradable magnesium alloy, a method for the production thereof and a use for implants, which allow the magnesium matrix of the implant to remain in an electrochemically stable state over the required support period with fine grain and high corrosion resistance without protective layers, while also improving the mechanical properties, such as increasing the tensile strength and proof stress, as well as reducing the mechanical asymmetry.

These objects are achieved by a magnesium alloy having the characteristics of claim 1, a method having the characteristics of claim 10, and the use according to the characteristics of claims 19 to 22. The characteristics listed in the dependent claims allow advantageous refinements of the magnesium alloy according to the invention, of the method for the production thereof according to the invention, and the use.

The solution according to the invention is based on the realization that the corrosion resistance and deformability of the magnesium matrix of the implant must be assured over the support period such that the implant is able to absorb multiaxial permanent load without fracture or cracking, and to also utilize the magnesium matrix as a means for the decomposition triggered by the physiological liquids.

This is achieved by the magnesium alloy comprising:

1.5 to 7.0% by weight Zn, 0.5 to 3.5% by weight Al, the remainder being magnesium which contains impurities, which promote electrochemical potential differences and/or the formation of precipitations and/or intermetallic phases, in a total amount of no more than 0.0063%) by weight of Fe, Si, Mn, Co, Ni, Cu, Zr, Y, Sc or rare earths having the ordinal numbers 21, 57 to 71 and 89 to 103, Be, Cd, In, Sn and/or Pb as well as P, wherein the alloy content of Zn in % by weight is greater than or equal to the alloy content of Al in % by weight.

The magnesium alloy according to the invention has extraordinarily high corrosion resistance, which is achieved by drastically reducing the content of impurities and the combinations thereof in the magnesium matrix, and by also adding precipitation and solid solution hardenable elements, which must be present in completely solid solution. The micro structure that is obtained has no electrochemical potential differences between the individual matrix phases after the forming and heat treatment processes, and therefore these differences cannot expedite the corrosion in physiological media.

The applicant surprisingly found that an alloy matrix, which has a content of Zn of preferably 1.5 to 5.5%> by weight, and more particularly 3.5 to 5.5%> by weight, and a content of Al of preferably at least 0.5 to 2.0% by weight, and more particularly 1.0 to 2.0% by weight, can form, or depending on the treatment forms, a mixed crystal from Zn and Al, which are present completely in solution form, without precipitations, the mixed crystal having a higher standard potential than unalloyed high-grade magnesium and therefore the alloy being more noble.

Care should be taken that the alloy contents of Zn and Al are exactly adjusted such that the content in solid solution is as high as possible, and therefore maximum corrosion protection is achieved, without exceeding the solubility limit. Typical forming temperatures for this alloy range between 270 and 330°C under these conditions. This prevents particles from forming in the alloy matrix, which could take on the functions of cathodes during the corrosion process and thus promote corrosion.

Another surprising result is that, at a content of Zn of preferably 3.0 to 7.0% by weight, and more particularly 4.0 to 6.0% by weight, and a content of Al of preferably 0.5 to 3.5%) by weight, and more particularly 1.5 to 2.5% by weight, an alloy is obtained which contains precipitations in the form of Mg3Zn3Al ₂ und MgZn and has an extremely small grain size, wherein the precipitations having a size of less than 1 μιη, and preferably 0.2 μιη, are located both on the grain boundaries and in the grain interior.

In this case, the alloying elements may be present in the alloy in amounts even slightly above the solubility limit. Controlled by the cooling conditions during the production of the alloy, the alloying elements are initially present in solution. During forming of the alloy at temperatures below the solubility limit, for example at 250°C, fine particles are precipitated during forming which prevent grain growth and then contribute to an increase in tensile strength, both due to particle hardening and grain refining hardening. Through subsequent aging of the formed semi- finished product at temperatures below the temperature at which the alloying elements go completely into solution, for example 200°C, it is also possible to precipitate fine particles, which continue to remain in the matrix during the later thermomechanical treatment steps so as to prevent grain growth and increase the strength.

The alloy according to the invention has particularly high corrosion resistance. This is achieved by drastically reducing the contents of certain elements, and combinations of certain elements, in the alloy matrix whereby a microstructure is obtained in which, contrary to all known technically available magnesium materials, electrochemical differences in potential no longer occur between the individual matrix phases, and these therefore no longer play a role in terms of an expedited corrosion of the material in physiological media.

The previously known tolerance limits for impurities do not take into account that wrought magnesium alloys often times are subjected to a thermo mechanical treatment, and more particularly to an extended annealing process, which creates near-equilibrium structures. The metallic elements bond by way of diffusion and form what are known as intermetallic phases, which have a different electrochemical potential, notably a considerably higher potential, than the magnesium matrix, and therefore these intermetallic phases act as cathodes and can trigger galvanic corrosion processes.

Because the alloy according to the invention contains Al, it is particularly important to limit not only elements such as Ni, Co or Cu, which in general have a considerable adverse effect on the corrosion resistance of magnesium alloys, but notably the elements Fe, Mn and Si.

When producing such an alloy according to the prior art, both a remainder of Fe and a remainder of Mn are left in the melt. In addition, such melts are not purified with respect to Si. However, Fe, Mn and Si have a very high tendency to form a ternary intermetallic Fe-Mn-Si phase, which has a very positive potential and thus constitutes a very effective cathode for the corrosion of the material. Moreover, Al additionally shifts the boundary in the melt at which iron begins to precipitate as iron particles or intermetallic particles with other elements toward drastically lower iron contents.

The applicant has found that a corrosion-stable alloy matrix can be achieved when complying with the following tolerance limits of individual impurities in % by weight: Fe, Si, Mn, Co, Ni, Cu each with <0.0005; Zr, Y each with <0.0003; Sc or

rare earths having the ordinal numbers 21, 57 to 71 and 89 to 103 in total

<0.001; Be, Cd, In, Sn and/or Pb each with <0.0003; and P <0.0002.

Preferably the corrosion-staple alloy matrix contains impurities in a total amount of no more than 0.0053 Gew.%, which can be achieved when complying with the following tolerance limits of individual impurities in % by weight:

Fe, Si, Mn each with <0.0005; Co, Ni, Cu each with <0.0002; Zr, Y each

with <0.0003; Sc or rare earths having the ordinal numbers 21, 57 to 71 and

89 to 103 in total <0.001 ; Be, Cd, In, Sn and/or Pb each with <0.0003; and P

<0.0001.

In particular preferred the corrosion-staple alloy matrix contains impurities in a total amount of no more than 0.0022 Gew.%, which can be achieved when complying with the following tolerance limits of individual impurities in % by weigh n:

Fe, Si, Mn each with <0.0002; Co, Ni, Cu, Zr, Y each with <0.0001 ; Sc or

rare earths having the ordinal numbers 21, 57 to 71 and 89 to 103 in total

<0.0005; Be, Cd, In, Sn and/or Pb each with <0.0001, and P <0.0001.

The formation of precipitations or particles which have a positive potential difference as compared to the matrix is entirely suppressed, or drastically reduced, if the sum of individual impurities consisting of Fe, Si, Mn, Co, Ni and Cu is no more than 0.0030%) by weight, preferably no more than 0.0021% by weight, and particularly preferably no more than 0.0009% by weight.

The particular advantage of the alloy according to the invention is that it no longer has any relevant contents of Fe, Si or Mn and only Zn and Al remain in the material, which increase the corrosion resistance of magnesium and increase the strength, however no elements are present which could form effective cathodes for corrosion processes. Such low concentrations moreover no longer allow a formation of intermetallic phases, which have a more positive electrochemical potential as compared to the matrix. Because the Zr content is considerably below that of the prior art, no Zr-rich phases can form, which are always more noble than the magnesium matrix and thus act as cathodic sites which promote corrosion.

By limiting the yttrium content, the tendency toward stress and vibration corrosion is advantageously decreased, counteracting a rapid weakening of the mechanical strength.

Because the chemical elements of a magnesium alloy from biodegradable implants are absorbed by the human body, additionally the amounts of highly toxic elements such as Be, CD, In, Sn and/or Pb as well as rare earths (elements having the ordinal numbers 21, 57 to 71 and 89 to 103) must be limited in the alloy so as to achieve high biocompatibility, while also suppressing the formation of intermetallic phases between these elements and magnesium, aluminum and zinc.

Such low concentrations thus also ensure that the magnesium matrix no longer contains any, or contains only small amounts of, precipitations or particle phases, which have a more positive electrochemical potential as compared to the matrix.

In the connection with solid solution hardening by Zn and Al, these precipitations or particles of the elements contained in the alloy according to the present application allow the tensile strength of the magnesium matrix to be increased and the electrochemical potential of the matrix to be raised, whereby a corrosion-decreasing effect is created, notably with respect to physiological media. The precipitations preferably have a size of no more than 1 μιη, and preferably of no more than 0.2 μιη, and are located on the grain boundaries and in the grain interior, whereby the movement of grain boundaries during thermal treatment as well as dislocations during deformation are impaired and the strength of the magnesium alloy is increased.

The magnesium alloy according to the present patent application achieves a tensile strength of >275 MPa, and preferably >300 MPa, a yield point of >200 MPa, and preferably >225 MPa, and a yield ratio of <0.8, and preferably <075, wherein the difference between the tensile strength and yield point is >50 MPa, and preferably >100 MPa, and the mechanical asymmetry is <1.25.

These significantly improved mechanical properties of the novel magnesium alloy assure that the implants, for example cardiovascular stents, are able to withstand the multiaxial permanent load in the implanted state over the entire support period, despite onsetting degradation of the magnesium matrix due to corrosion.

So as to minimize the mechanical asymmetry, it is particularly important for the magnesium alloy to have a particularly fine micro structure having a grain size of no more than 7.5 μιη, preferably < 5 μιη, and particularly preferably < 2.5 μιη.

The objects are moreover achieved by a method for producing a magnesium alloy having improved mechanical and electrochemical properties. The method comprises the following steps:

a) generating high-purity magnesium by way of vacuum distillation;

b) generating a billet of the alloy by synthesis of the magnesium according to step a) with high-purity Zn and Al in a composition of 1.5 to 7.0% by weight Zn, 0.5 to 3.5% by weight Al, the remainder being magnesium containing impurities, which promote electrochemical potential differences and/or the formation of precipitations and/or intermetallic phases, in a total amount of no more than 0.0063% by weight of Fe, Si, Mn, Co, Ni, Cu, Zr, Y and Sc or rare earths having the ordinal numbers 21, 57 to 71 and 89 to 103, Be, Cd, In, Sn and/or Pb as well as P, wherein the alloy content of Zn in % by weight is greater than or equal to the alloy content of Al in % by weight;

c) homogenizing the alloy by annealing at a temperature between 250°C and 350°C with a holding period of 1 to 60 hours and cooling by exposure to air and in a water bath;

c) at least single forming of the homogenized alloy in the temperature range between 250°C and 350°C; and

d) optionally heat treating the formed alloy in the temperature range between 200°C and 350°C with a holding period of 5 minute to 6 hours. In a preferred embodiment, step c) is performed alloy in the temperature range between 270°C and 350°C.

A content of Zn of preferably 1.5 to 5.5% by weight, and more particularly 3.5 to 5.5% by weight, and a content of Al of preferably at least 0.2 to 2.0% by weight, and more particularly 1.0 to 2.0% by weight, assures that the microstructure of the alloy is a mixed crystal made of Zn and Al, which are present completely in solution form, without precipitations, the mixed crystal having a higher standard potential than the high-grade magnesium. During subsequent forming, care must be taken that the forming temperature, for example 270°C to 330°C, is adhered to so as to ensure that the solubility limit for the individual elements is not exceeded. This prevents particles from forming in the matrix, which can have a corrosion-accelerating effect.

In contrast, a content of Zn of preferably 3.0 to 7.0% by weight, and more particularly 4.0 to 6.0%) by weight, and a content of Al of preferably 0.5 to 3.5% by weight, and more particularly 1.5 to 2.5% by weight means that the alloying element may be present in amounts slightly higher than the solubility limit. The shaping process, after homogenizing annealing, at temperatures of 200°C to 350°C below the solubility limit according to step d) prevents precipitations in the Mgi ₇ Ali ₂ phase and causes only fine particles to be precipitated in the matrix in the form of Mg ₃ Zn ₃ Al ₂ und MgZn, which impair grain growth and contribute to an increase in the tensile strength of the alloy due to particle hardening and grain refining hardening. Through subsequent aging of the formed semifinished product below temperatures at which the alloying elements are caused to go completely into solution (typically, these are temperatures of 20°C to 325°C), it is possible to precipitate particles, which continue to remain in the matrix during the later thermomechanical treatment, prevent grain growth processes and further increase the strength.

Vacuum distillation is preferably used to produce a starting material for the alloy according to the present patent application having the required threshold values.

The quantities of the alloying elements Zn and Al as well as the sum of impurities can be selectively adjusted and in % by weight are: for the individual impurities:

Fe, Si, Mn, Co, Ni, Cu each with <0.0005;

Zr, Y each with <0.0003;

Sc or rare earths having the ordinal numbers 21, 57 to 71 and 89 to 103

in total <0.001;

Be, Cd, In, Sn and/or Pb each with <0.0003; and

P <0.0002. aa) for the individual impurities in a preferred total amount of impurities of no more than 0.0053% by weight,:

Fe, Si, Mn each with <0.0005;

Co, Ni, Cu each with <0.0002;

Zr, Y each with <0.0003;

Sc or rare earths having the ordinal numbers 21, 57 to 71 and 89 to

103 in total <0.001;

Be, Cd, In, Sn and/or Pb each with <0.0003; and

P O.0001. ab) for the individual impurities in a particularly preferred total amount of impurities of no more than 0.0022% by weight:

Fe, Si, Mn each with <0.0002;

Co, Ni, Cu, Zr, Y each with <0.0001 ;

Sc or rare earths having the ordinal numbers 21 , 57 to 71 and 89 to

103 in total O.0005;

Be, Cd, In, Sn and/or Pb each with O.0001 ; and

P O.0001.

for the combination of individual impurities in total:

Fe, Si, Mn, Co, Ni and Cu no more than 0.0040, preferably no more than 0.0020, and particularly preferably no more than 0.0010. It is particularly advantageous that the method described here only requires a small number of forming steps. Extrusion, equal channel angular extrusion and/or multiple forging can thus preferably be employed, which assure that a substantially homogeneous fine grain of <15 μιη is achieved.

Because of the artificial aging, precipitations having a grain size of 1 μιη, and preferably 0.2 μιη, form on the grain boundaries and in the interior of the grains, whereby the tensile strength of the alloy reaches values which at >275 MPa, and preferably >300 MPa, are considerably higher than the prior art.

A third concept of the patent application relates to the use of the magnesium alloy produced according to the method, which has the aforedescribed advantageous composition and structure, in medical technology, notably for the production of implants, for example endovascular implants such as stents, for fastening and temporarily fixing tissue implants and tissue transplantations, orthopedic and dental implants, and neuro implants.

All implants in the sense of this patent application are in the Cardiovascular field, osteosynthesis field or other areas.

Cardiovascular field in the sense of this application means

the field of diagnostic, prevention and treatment of all diseases of the cardiovascular system, i.e. heart and blood vessel system,

by mean of active and non-active implants used to support vessels, and vein systems including coronary, cerebral and peripheral vascular implants like stents, valves, closure devices, occluders, clips, coils, staples, implantable regional drug delivery devices,

implantable electrostimulators (like pacemakers and defibrillators), implantable monitoring devices, implantable electrodes,

system for fastening and temporarily fixing tissue implants and tissue transplantations

field also includes any type of stent as mechanical fix or temporary scaffold to support hollow organs (or bodies?) including bones, intervertebral disks Osteosynthesis in the sense of this application means

the field of treatment of fractured bones for internal fixation and stabilization by mechanical devices such as metal plates, pins, rods, wires, screws, clips, nails, staples excluding stent technology

Examples of areas out of the osteosynthesis field or the cardiovascular field are:

Devices for the treatment of diseases of the sinews, joints, muscles, cartilages, oral (including dental) and maxillo facial implants (excl. osteosynthesis means), esthetic implants,

supporting tools out of the body, (examples?)

tissue engineering,

soft tissue implants,

devices for wound care,

suture material and clamps,

neurosurgery

local drug delivery (excl. cardiovascular, i.e. lever)

renal

Exemplary embodiments Example 1

A magnesium alloy is to be generated which is composed of 5% by weight Zn and 2% by weight Al, the remainder being Mg, in which the alloying elements are present completely in solution form, and which contains the following individual impurities in % by weight:

Fe: <0.0005; Si: <0.0005; Mn: <0.0005; Co: <0.0002; Ni: <0.0002; Cu <0.0002, wherein the sum of impurities consisting of Fe, Si, Mn, Co, Ni and Cu should be no more than 0.0021% by weight, the content of Zr < 0.0003% by weight, the content of Y <0.0001% by weight, the content of rare earths having the ordinal numbers 21, 39, 57 to 71 and 89 to 103 in total should be less than 0.001% by weight, and the contents of Be and Cd should be no more than 0.0001% by weight, respectively, and P <0.0001. This alloy, produced using magnesium vacuum distillation, is subjected to homogenizing annealing at a temperature of 300°C for a duration of 48 hours, and subsequently to a forming process at a temperature of 275°C to 300°C, which is above the solubility limit. A precision tube for a cardiovascular stent is produced by multiple extrusion and annealing processes above the solubility limit at 275°C so as to prevent the precipitation of Mg ₃ Zn ₃ Al ₂ particles.

The grain size that was achieved was < 10 μιη, and the magnesium alloy reached a tensile strength of more than 300 MPa and proof stress of < 230 MPa. The yield ratio was 0.72 and the mechanical asymmetry was 1.15.

Example 2

A magnesium alloy is to be produced, which is composed of 5.5% by weight Zn and 3% by weight Al, the remainder being magnesium, in which some of the alloying elements are present as particles in the form of MgZnAl having a size of < 0.5 μιη, and which contains the following individual impurities in % by weight:

Fe: <0.0005; Si: <0.0005; Mn: <0.0005; Co: <0.0002; Ni: <0.0002; Cu <0.0002, wherein the sum of impurities consisting of Fe, Si, Mn, Co, Ni and Cu should be no more than 0.0021% by weight, the content of Zr < 0.0003% by weight, the content of Y <0.0001% by weight, the content of rare earths having the ordinal numbers 21, 39, 57 to 71 and 89 to 103 in total should be less than 0.001% by weight, and the contents of Be and Cd should be no more than 0.0001% by weight, respectively, and P <0.0001.

The magnesium alloy is produced in a manner which corresponds to that of Example 1. So as to precipitate some of the MgZnAl particles, an extrusion process is carried out above the solubility limit at temperatures of < 275°C. The precision tubes for a cardiovascular stent were produced by multiple extrusion and annealing processes, in part below the solubility limit. The solubility limit was 330°C. This alloy according to the subject matter of the patent application reached the following properties:

- tensile strength of 310 to 340 MPa;

proof stress of≤ 230 MPa;

a yield ratio of 0.69;

mechanical asymmetry of 1.1 ; and

a grain size of < 5 μιη.