CA2663605C - Magnesium gadolinium alloys - Google Patents
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Abstract
This invention relates to gadolinium-containing magnesium alloys, particularly those which possess high strength combined with corrosion resistance, and an optimised balance of strength and ductility. The described alloys consist of 2.0 to 5.0, preferably 2.3 to 4.6, at% in total of gadolinium and at least one of soluble heavy lanthanides and yttrium, wherein the ratio of the aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, and preferably approximately 1.5:1, from 0 up to 0.3 at% of zirconium, preferably at least 0.03 at%, optionally with zinc, wherein when zinc is present the amount of zinc is such that the ratio of the weight of zinc to the weight of zirconium is preferably less than 2:1, and more preferably less than 0.75:1, all other lanthanides, viz. lanthanum, cerium, praseodymium, neodymium, promethium, samarium, europium and ytterbium in an aggregate amount of less than at 0.2 at%, and preferably less than 0.1 at%, the balance being magnesium, with any other element being present in an amount of no more than 0.2 at%, and preferably no more than 0.1 at%, and more preferably being present only as an incidental impurity.
Description
MAGNESIUM GADOLINIUM ALLOYS
This invention relates to gadolinium-containing magnesium alloys, particularly those which possess high strength combined with corrosion resistance, and an optimised balance of strength and ductility. The described alloys also have exceptional high temperature performance for magnesium alloys. The alloys of the present invention have been developed as extrusion alloys, but can be rolled to produce sheets and are also suitable for forging and machining. Although they can be cast successfully to form billets, these alloys are not as suitable to use as shape casting alloys in processes such as die casting or sand casting as other magnesium alloys due to a tendency to form cracks.
There is considerable prior art concerning the Mg-Y-Gd system. ' The United States patent US3391034 teaches that binary alloys of magnesium and 8 to llwts yttrium can be produced that are age-hardenable.
It states that the ductility of these alloys is inversely proportional to their yield strength, and that an acceptable ductility is greater than 3-5%. It teaches that for the magnesium yttrium system levels of yttrium less than 8wt% do not produce sufficient mechanical properties compared with other magnesium alloys.
The mechanical properties claimed in US3391034 are shown in Table 1.
This invention relates to gadolinium-containing magnesium alloys, particularly those which possess high strength combined with corrosion resistance, and an optimised balance of strength and ductility. The described alloys also have exceptional high temperature performance for magnesium alloys. The alloys of the present invention have been developed as extrusion alloys, but can be rolled to produce sheets and are also suitable for forging and machining. Although they can be cast successfully to form billets, these alloys are not as suitable to use as shape casting alloys in processes such as die casting or sand casting as other magnesium alloys due to a tendency to form cracks.
There is considerable prior art concerning the Mg-Y-Gd system. ' The United States patent US3391034 teaches that binary alloys of magnesium and 8 to llwts yttrium can be produced that are age-hardenable.
It states that the ductility of these alloys is inversely proportional to their yield strength, and that an acceptable ductility is greater than 3-5%. It teaches that for the magnesium yttrium system levels of yttrium less than 8wt% do not produce sufficient mechanical properties compared with other magnesium alloys.
The mechanical properties claimed in US3391034 are shown in Table 1.
2 Table 1 Yttrium Content Yield Stress UTS Elongation (wt o) (Mpa) (Mpa) o 8.2 303 344 3 9.0 323 374 6 10.6 335 374 5 The Russian patent SU1010880 teaches about magnesium alloys containing yttrium and gadolinium, optionally with zirconium. The two specific alloys discussed in the patent specification have the mechanical properties summarised in Table 2.
Table 2 Alloy Composition (wt%) Yield Stress UTS Elongation (MPa) (MPa) (%) 4-6% Y, 8-10% Gd,0.3-1.0% Mn 378-390 393-442 4.4-9.8 5-6.5% Y, 3.5-5.5% Gd, 0.15-0.7% Zr 353-387 397-436 4.0-6.0 This prior art teaches that these types of manganese-containing alloy form cracks while casting, but that this effect is reduced by the replacement of the manganese with zirconium. This teaching is silent regarding the corrosion behaviour or isotropy of these alloys.
The Japanese patent JP10147830 teaches that an alloy containing 1-<6 wt% Gd and 6-12 wt% Y produces good strength at high temperature. Zirconium in an amount of up to 2 wt% can also be present.
Also the Japanese patent JP9263871 teaches that an alloy containing 0.8-5 wt% Y and 4-15 wt% Gd or Dy produces a product that can be forged to produce an alloy of good strength. There is however no recognition in this document of the importance of not only the amount of each alloying element but their respective ratios.
Table 2 Alloy Composition (wt%) Yield Stress UTS Elongation (MPa) (MPa) (%) 4-6% Y, 8-10% Gd,0.3-1.0% Mn 378-390 393-442 4.4-9.8 5-6.5% Y, 3.5-5.5% Gd, 0.15-0.7% Zr 353-387 397-436 4.0-6.0 This prior art teaches that these types of manganese-containing alloy form cracks while casting, but that this effect is reduced by the replacement of the manganese with zirconium. This teaching is silent regarding the corrosion behaviour or isotropy of these alloys.
The Japanese patent JP10147830 teaches that an alloy containing 1-<6 wt% Gd and 6-12 wt% Y produces good strength at high temperature. Zirconium in an amount of up to 2 wt% can also be present.
Also the Japanese patent JP9263871 teaches that an alloy containing 0.8-5 wt% Y and 4-15 wt% Gd or Dy produces a product that can be forged to produce an alloy of good strength. There is however no recognition in this document of the importance of not only the amount of each alloying element but their respective ratios.
3 Using peak hardness as a measure some tests were carried out on alloys with constant values of atomic percent rare earths (Total Rare Earths), while varying the ratio of yttrium plus other soluble lanthanides to gadolinium.
The results are as follows:
Melt At%Gd At% Y+ At% Ratio of Y Wt% Wt%Y+ Peak Number other TRE + other Gd Other Hardness soluble soluble soluble (Hv) lanthanides lanthanides lanthanides to Gd DF9122 1.33 2.00 3.33 1.5 7.6 6.5 127 DF9123 0.83 2.50 3.33 3.0 4.8 8.2 110 DF9124 2.50 0.83 3.33 0.3 13.1 2.6 118 JP9263871 also discusses the addition of Ca and other lanthanides, but we have found that the addition of Ca and certain lanthanides is very deleterious to these types of alloys.
The Chinese patent CN1676646 purports to teach that a broad range of alloys containing 1-6 wt% Y, 6-15wt% Gd, 0.35-0.8 wt% Zr and 0-1.5 wt% Ca can be extruded to produce extrudates of good strength, but there is little specific description of the alloys of the Examples and no.
clear demonstration of the utility of the described alloys near the limits of the claimed range.
All this prior art seems to be focussed on maximising the strength of the alloy at the expense of its ductility, but this latter is an equally important material property. Furthermore there is no recognition in the prior art of the effect of the levels of the different alloying element on the corrosion behaviour of the described alloys. What the present invention teaches is a way to obtain improved ductility while also achieving
The results are as follows:
Melt At%Gd At% Y+ At% Ratio of Y Wt% Wt%Y+ Peak Number other TRE + other Gd Other Hardness soluble soluble soluble (Hv) lanthanides lanthanides lanthanides to Gd DF9122 1.33 2.00 3.33 1.5 7.6 6.5 127 DF9123 0.83 2.50 3.33 3.0 4.8 8.2 110 DF9124 2.50 0.83 3.33 0.3 13.1 2.6 118 JP9263871 also discusses the addition of Ca and other lanthanides, but we have found that the addition of Ca and certain lanthanides is very deleterious to these types of alloys.
The Chinese patent CN1676646 purports to teach that a broad range of alloys containing 1-6 wt% Y, 6-15wt% Gd, 0.35-0.8 wt% Zr and 0-1.5 wt% Ca can be extruded to produce extrudates of good strength, but there is little specific description of the alloys of the Examples and no.
clear demonstration of the utility of the described alloys near the limits of the claimed range.
All this prior art seems to be focussed on maximising the strength of the alloy at the expense of its ductility, but this latter is an equally important material property. Furthermore there is no recognition in the prior art of the effect of the levels of the different alloying element on the corrosion behaviour of the described alloys. What the present invention teaches is a way to obtain improved ductility while also achieving
4 high strength levels, without sacrificing corrosion resistance. None of this prior art recognises that when two or more of lanthanides and yttrium are in the same alloy, it is the specific ratio of their atomic concentrations that is the key factor in the effectiveness of the additions.
By selecting alloying additions within the range claimed in this invention and controlling the isotropy of the alloy, in addition to these improved mechanical properties, the alloys of the present invention will generally have corrosion rates of less than 100 mils per year (mpy) in the industry standard ASTM B117 salt-fog test, and preferably less than 50 mpy. Since the above prior art does not mention the corrosion performance of the described alloys and so it can be assumed that this feature of the described alloys was in line with conventional alloys, i.e. inferior to that of the alloys of the present invention and greater than a corrosion rate of 50 mpy.
In particular, in the academic published work by Rokhlin, namely the book entitled "Magnesium Alloys Containing Rare Earth Metals" Rokhlin, L L, published 2003, the inventor of SU1010880 states that increasing the yttrium content of magnesium alloys is detrimental to the corrosion rate of the alloy as shown in Table 3. The text states that this is due to the presence of Mgz4Y5 compounds which are cathodic to the solid solution.
Table 3 Yttrium Content Corrosion Rate Wt% mg/cm2/hour Mills/years 0.5 0.025 48 3.8 0.14 268 10.5 0.36 690 In accordance with the present invention there is provided a magnesium alloy consisting of:
2.0 to 5.0, preferably 2.3 to 4.6, at% in total of gadolinium and at least one element selected from
By selecting alloying additions within the range claimed in this invention and controlling the isotropy of the alloy, in addition to these improved mechanical properties, the alloys of the present invention will generally have corrosion rates of less than 100 mils per year (mpy) in the industry standard ASTM B117 salt-fog test, and preferably less than 50 mpy. Since the above prior art does not mention the corrosion performance of the described alloys and so it can be assumed that this feature of the described alloys was in line with conventional alloys, i.e. inferior to that of the alloys of the present invention and greater than a corrosion rate of 50 mpy.
In particular, in the academic published work by Rokhlin, namely the book entitled "Magnesium Alloys Containing Rare Earth Metals" Rokhlin, L L, published 2003, the inventor of SU1010880 states that increasing the yttrium content of magnesium alloys is detrimental to the corrosion rate of the alloy as shown in Table 3. The text states that this is due to the presence of Mgz4Y5 compounds which are cathodic to the solid solution.
Table 3 Yttrium Content Corrosion Rate Wt% mg/cm2/hour Mills/years 0.5 0.025 48 3.8 0.14 268 10.5 0.36 690 In accordance with the present invention there is provided a magnesium alloy consisting of:
2.0 to 5.0, preferably 2.3 to 4.6, at% in total of gadolinium and at least one element selected from
5 the group consisting of soluble heavy lanthanides and yttrium, wherein the ratio of the aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, and preferably approximately 1.5:1, from 0 up to 0.3 at% of zirconium, preferably at least 0.03 at %, optionally with zinc, wherein when zinc is present the amount of zinc is such that the ratio of the weight of zinc to the weight of zirconium is preferably less than 2:1, and more preferably less than 0.75:1, all other lanthanides, viz. lanthanum, cerium, praseodymium, neodymium, promethium, samarium, europium and ytterbium, in an aggregate amount of less than at 0.2 at%, and preferably less than 0.1 at%, the balance being magnesium, with any other element being present in an amount of no more than 0.2 at%, preferably no more than 0.1 at%, and more preferably being present only as an incidental impurity.
In this specification soluble heavy lanthanides are defined as elements with atomic numbers 65 to 69 inclusive and 71. Soluble heavy lanthanides (SHL) are those which display substantial solid solubility in magnesium. They are terbium, dysprosium, holmium,
In this specification soluble heavy lanthanides are defined as elements with atomic numbers 65 to 69 inclusive and 71. Soluble heavy lanthanides (SHL) are those which display substantial solid solubility in magnesium. They are terbium, dysprosium, holmium,
6 erbium, thulium and lutetium. These elements are characterised by all of them having the same hexagonal close packed metallic structure as possessed by yttrium and magnesium, and by having a metallic radius of between 0.178nm and 0.173nm. They also exist only in a trivalent state when oxidised, which thus distinguishes them from elements such as europium and ytterbium which show both tri- and bivalency and do not show any appreciable solid solubility in magnesium. When present the aggregate level of soluble heavy lanthanides should be greater than 0.1 at% in order ot contribute significantly to the mechanical properties of the alloy. A particularly preferred soluble heavy lanthanide is erbium.
It is well known that the strengthening of alloys by precipitation hardening is a function of the amount and type of particles that are formed. This effect is related to both the amount of alloying elements that can be dissolved in the matrix expressed as atomic percent .20 and not as weight percent, and to the potential to precipitate intermetallic particles by heat treatment.
The binary phase diagrams for the soluble heavy lanthanides and magnesium, for yttrium and magnesium, and for gadolinium and magnesium all show this potential.
From these phase diagrams it has been assumed to date that the soluble heavy lanthanides, gadolinium and yttrium will all strengthen magnesium in similar ways.
It has, however, surprisingly been found that when gadolinium is present in a specific amount the addition of a soluble heavy lanthanide or yttrium within a defined range causes the formation of at least one indeterminate ternary phase which affects the alloy's mechanical properties. This at least one ternary phase requires a ratio between the soluble heavy lanthanide or yttrium and
It is well known that the strengthening of alloys by precipitation hardening is a function of the amount and type of particles that are formed. This effect is related to both the amount of alloying elements that can be dissolved in the matrix expressed as atomic percent .20 and not as weight percent, and to the potential to precipitate intermetallic particles by heat treatment.
The binary phase diagrams for the soluble heavy lanthanides and magnesium, for yttrium and magnesium, and for gadolinium and magnesium all show this potential.
From these phase diagrams it has been assumed to date that the soluble heavy lanthanides, gadolinium and yttrium will all strengthen magnesium in similar ways.
It has, however, surprisingly been found that when gadolinium is present in a specific amount the addition of a soluble heavy lanthanide or yttrium within a defined range causes the formation of at least one indeterminate ternary phase which affects the alloy's mechanical properties. This at least one ternary phase requires a ratio between the soluble heavy lanthanide or yttrium and
7 PCT/GB2007/003491 gadolinium of 3:2. Alloys having this ratio demonstrate a better combination of mechanical properties, namely strength, ductility and transverse properties, than can be achieved using other combinations of amounts of the lanthanides, yttrium and gadolinium. Significantly improved properties can be found where the ratio is between 1.25:1 and 1.75:1 for alloys which contain from 2.3 to 4.6 at% in total of gadolinium and at least one of soluble heavy lanthanide or yttrium. Outside this range either the strength and/or the ductility of the alloys declines. This decline becomes noticeable when the total amount of gadolinium, soluble heavy lanthanide and yttrium is below 2.0 at% and above 5.0 at%.
In order to assist this precipitation hardening effect a grain refining element can be added in an amount up to its solid solubility limit in the alloy. A preferred such element is zirconium. This can be added with increasing amounts generally improving the alloy's yield stress and elongation-to-failure properties. For such an effect at least 0.03 atomic per cent of zirconium should be present, and the maximum amount is the solid solubility limit of Zr in the alloy which is generally at about 0.3 atomic percent. However with both high and low levels of zirconium corrosion resistance may decline.
The most preferred composition for a zirconium containing alloy of the present invention is 5.5 to 6.5 wt% Y, 6.5 to 7.5 wt% Gd and 0.2 to 0.4 wt% Zr, with the remainder being magnesium and incidental impurities. For some alloy compositions the level of zirconium should be from 0.3 to below 0.35% by weight in order to pass the 50 mpy salt-fog test.
In order to assist this precipitation hardening effect a grain refining element can be added in an amount up to its solid solubility limit in the alloy. A preferred such element is zirconium. This can be added with increasing amounts generally improving the alloy's yield stress and elongation-to-failure properties. For such an effect at least 0.03 atomic per cent of zirconium should be present, and the maximum amount is the solid solubility limit of Zr in the alloy which is generally at about 0.3 atomic percent. However with both high and low levels of zirconium corrosion resistance may decline.
The most preferred composition for a zirconium containing alloy of the present invention is 5.5 to 6.5 wt% Y, 6.5 to 7.5 wt% Gd and 0.2 to 0.4 wt% Zr, with the remainder being magnesium and incidental impurities. For some alloy compositions the level of zirconium should be from 0.3 to below 0.35% by weight in order to pass the 50 mpy salt-fog test.
8 It has been found that the presence of small amounts of zinc are beneficial to the corrosion performance of the alloys of the present invention, but that as the level of zinc is increased the alloy's corrosion performance deteriorates. Preferably the level of zinc should be from 0.07 to below 0.5at%. There also appears to be a linkage regarding the formation of different types of precipitates when both zirconium and zinc are present in the alloy, and it has been found that the ratio of zinc to zirconium should not exceed 2:1, and should be preferably less than 0.75:1.
Any lanthanide other than the required soluble heavy lanthanide or yttrium should be present in a total amount of less than 0.2 atomic per cent, and preferably below 0.1 at%, otherwise there is interference with the formation of the desired at least one indeterminate ternary phase as described above. Similarly any other element should be present in an amount of no more than 0.2 at%, preferably no more than 0.1 at%, and more preferably be present only at an incidental impurity level.
The alloys of the present invention may be used for extrusions, sheet, plate and forgings. Additionally they may be used for parts machined and/or manufactured from extrusions, sheet, plate or forgings.
Examples A magnesium alloy DF8791 was produced containing 3.04 at % in total of yttrium and gadolinium, where the yttrium to gadolinium ratio was 1.52:1. Additionally it
Any lanthanide other than the required soluble heavy lanthanide or yttrium should be present in a total amount of less than 0.2 atomic per cent, and preferably below 0.1 at%, otherwise there is interference with the formation of the desired at least one indeterminate ternary phase as described above. Similarly any other element should be present in an amount of no more than 0.2 at%, preferably no more than 0.1 at%, and more preferably be present only at an incidental impurity level.
The alloys of the present invention may be used for extrusions, sheet, plate and forgings. Additionally they may be used for parts machined and/or manufactured from extrusions, sheet, plate or forgings.
Examples A magnesium alloy DF8791 was produced containing 3.04 at % in total of yttrium and gadolinium, where the yttrium to gadolinium ratio was 1.52:1. Additionally it
9 contained 0.15 at% zirconium, with other elements being at impurity levels.
Another magnesium alloy, DF8961, was produced containing 2.65 at% in total of yttrium and gadolinium, with an yttrium to gadolinium ratio of 1.46:1. Additionally, it contained 0.12 at% Zr and 0.08 at% Zn, with other elements being at impurity levels.
Another magnesium alloy DF9380 was produced containing a a 3.03 at% of a mixture of erbium, gadolinium and yttrium with a soluble rare earth plus yttrium to gadolinium ratio of 1.38:1. Additionally it contained 0.125 at%
zirconium.
All these alloys possessed yield stresses greater than 300MPa and elongations-to-failure greater than or equal to 10 0 .
Three further magnesium alloys were tested, namely alloys DF8915, DF9386 and DF8758, which had similar total levels of yttrium and gadolinium to those of DF8961 but in different ratios. DF8915 had a significantly higher ratio of 3.9:1 and this produced a reduced yield stress of only 25OMPa. DF9386 and DF8758 both had a significantly lower ratio of 0.72:1 and 0.93:1 respectively. These low ratios had the effect of reducing the ductility of these alloys to below 5% to levels that are commercially unacceptable for this type of product.
A further alloy magnesium alloy DF9381 was produced containing 2.99 at% of a mixture of ytterbium, gadolinium and yttrium with a soluble rare earth plus yttrium to gadolinium ratio of 1.39:1. Additionally it contained 0.121 at% zirconium. The ytterbium in this alloy is not a soluble heavy lanthanide, and as a result of its addition to the alloy the strength of the alloy was reduced to unacceptably low levels.
A further set of test alloys were produced to examine the effect of zirconium on corrosion for the alloys of the present invention. Melts DF9382a to DF9382e all had the same composition except for varying levels of zirconium.
Another magnesium alloy, DF8961, was produced containing 2.65 at% in total of yttrium and gadolinium, with an yttrium to gadolinium ratio of 1.46:1. Additionally, it contained 0.12 at% Zr and 0.08 at% Zn, with other elements being at impurity levels.
Another magnesium alloy DF9380 was produced containing a a 3.03 at% of a mixture of erbium, gadolinium and yttrium with a soluble rare earth plus yttrium to gadolinium ratio of 1.38:1. Additionally it contained 0.125 at%
zirconium.
All these alloys possessed yield stresses greater than 300MPa and elongations-to-failure greater than or equal to 10 0 .
Three further magnesium alloys were tested, namely alloys DF8915, DF9386 and DF8758, which had similar total levels of yttrium and gadolinium to those of DF8961 but in different ratios. DF8915 had a significantly higher ratio of 3.9:1 and this produced a reduced yield stress of only 25OMPa. DF9386 and DF8758 both had a significantly lower ratio of 0.72:1 and 0.93:1 respectively. These low ratios had the effect of reducing the ductility of these alloys to below 5% to levels that are commercially unacceptable for this type of product.
A further alloy magnesium alloy DF9381 was produced containing 2.99 at% of a mixture of ytterbium, gadolinium and yttrium with a soluble rare earth plus yttrium to gadolinium ratio of 1.39:1. Additionally it contained 0.121 at% zirconium. The ytterbium in this alloy is not a soluble heavy lanthanide, and as a result of its addition to the alloy the strength of the alloy was reduced to unacceptably low levels.
A further set of test alloys were produced to examine the effect of zirconium on corrosion for the alloys of the present invention. Melts DF9382a to DF9382e all had the same composition except for varying levels of zirconium.
10 Alloy DF9382a shows that if the material is zirconium free (i.e. below detectable limits with standard industrial spark emission spectroscopy) the corrosion rate is above the acceptable level of 50 mils per year corrosion in the standard salt fog test. Further, at higher levels of zirconium for this alloy, DF9382b and DF9382c also show this poor behaviour. However at levels of zirconium between 0.03 at % (0.1 wt %) and 0.12 at %
(0.4 wt%) good corrosion performance is achieved. This is demonstrated by DF9382d and DF9382e.
A summary of these test results is shown in Table 4, in which some of the data has been rounded.
(0.4 wt%) good corrosion performance is achieved. This is demonstrated by DF9382d and DF9382e.
A summary of these test results is shown in Table 4, in which some of the data has been rounded.
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Claims (14)
1. A magnesium alloy comprising:
2.0 to 5.0 at% in total of gadolinium and at least one element selected from the group consisting of soluble heavy lanthanides and yttrium, wherein the soluble heavy lanthanides are terbium, dysprosium, holmium, erbium, thulium and lutetium, and wherein the ratio of an aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, all other lanthanides in an aggregate amount of less than 0.2 at %, wherein the alloy additionally contains zirconium in an amount of from 0.06 to 0.12 at%, and wherein at least one soluble heavy lanthanide is present in an amount of at least 0.1 at%, the balance being magnesium, with any other element being present only as an incidental impurity in an amount of less than 0.2 at%.
2.0 to 5.0 at% in total of gadolinium and at least one element selected from the group consisting of soluble heavy lanthanides and yttrium, wherein the soluble heavy lanthanides are terbium, dysprosium, holmium, erbium, thulium and lutetium, and wherein the ratio of an aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, all other lanthanides in an aggregate amount of less than 0.2 at %, wherein the alloy additionally contains zirconium in an amount of from 0.06 to 0.12 at%, and wherein at least one soluble heavy lanthanide is present in an amount of at least 0.1 at%, the balance being magnesium, with any other element being present only as an incidental impurity in an amount of less than 0.2 at%.
2. An alloy as claimed in claim 1 wherein the total amount of gadolinium, at least one soluble heavy lanthanide and yttrium is 2.3 to 4.6 at%.
3. An alloy as claimed in claim 1 or claim 2 wherein the said ratio is approximately 1.5:1.
4. An alloy as claimed in any one of claims 1 to 3 wherein the at least one soluble heavy lanthanide is erbium.
5. An alloy as claimed in any one of claims 1 to 4 wherein all other lanthanides are present in an aggregate amount of less than 0.1 at%.
6. An alloy as claimed in any one of claims 1 to 5 wherein any other element is present in the amount of less than 0.1 at%.
7. A magnesium alloy comprising:
2.0 to 5.0 at% in total of gadolinium and at least one element selected from the group consisting of soluble heavy lanthanides and yttrium, wherein the soluble heavy lanthanides are terbium, dysprosium, holmium, erbium, thulium and lutetium, and wherein the ratio of an aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, all other lanthanides in an aggregate amount of less than 0.2 at %, wherein the alloy additionally contains zirconium in an amount of from 0.06 to 0.12 at%, and containing zinc in an amount of from 0.06 to 0.6 at%, wherein at least one soluble heavy lanthanide is present in an amount of at least 0.1 at%, the balance being magnesium, with any other element being present only as an incidental impurity in an amount of less than 0.2 at%.
2.0 to 5.0 at% in total of gadolinium and at least one element selected from the group consisting of soluble heavy lanthanides and yttrium, wherein the soluble heavy lanthanides are terbium, dysprosium, holmium, erbium, thulium and lutetium, and wherein the ratio of an aggregate amount of soluble heavy lanthanides and yttrium to the amount of gadolinium is between 1.25:1 and 1.75:1, all other lanthanides in an aggregate amount of less than 0.2 at %, wherein the alloy additionally contains zirconium in an amount of from 0.06 to 0.12 at%, and containing zinc in an amount of from 0.06 to 0.6 at%, wherein at least one soluble heavy lanthanide is present in an amount of at least 0.1 at%, the balance being magnesium, with any other element being present only as an incidental impurity in an amount of less than 0.2 at%.
8. An alloy as claimed in claim 7 wherein zinc is present in an amount of from 0.07 to less than 0.5at%.
9. An alloy as claimed in any one of claims 1 to 8 additionally containing a grain refining element in an amount up to its solid solubility limit in the alloy.
10. An alloy as claimed in claim 9 wherein zirconium is present in an amount of from 0.06 to 0.1 at%.
11. An alloy as claimed in claim 9 or claim 10 additionally containing zinc wherein the amount of zinc is such that the ratio of the weight of zinc to the weight of zirconium is less than 2:1.
12. An alloy as claimed in claim 11 wherein the zinc/zirconium ratio is less than 0.75:1.
13. An alloy as claimed in any one of claims 1 to 12 having a corrosion rate less than 50 mils per year in a standard salt-fog test.
14. An alloy as claimed in any one of claims 1 to 13 in the form of an extrusion, sheet, plate forging or mechanical part.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB0617970.9 | 2006-09-13 | ||
| GBGB0617970.9A GB0617970D0 (en) | 2006-09-13 | 2006-09-13 | Magnesium gadolinium alloys |
| PCT/GB2007/003491 WO2008032087A2 (en) | 2006-09-13 | 2007-09-12 | Magnesium gadolinium alloys |
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| CA2663605A1 CA2663605A1 (en) | 2008-03-20 |
| CA2663605C true CA2663605C (en) | 2016-07-19 |
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| CA2663605A Expired - Fee Related CA2663605C (en) | 2006-09-13 | 2007-09-12 | Magnesium gadolinium alloys |
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| EP (1) | EP2074236B1 (en) |
| JP (1) | JP5309031B2 (en) |
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| GB (1) | GB0617970D0 (en) |
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| RU (1) | RU2450068C2 (en) |
| TW (1) | TWI426137B (en) |
| WO (1) | WO2008032087A2 (en) |
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| GB0817893D0 (en) | 2008-09-30 | 2008-11-05 | Magnesium Elektron Ltd | Magnesium alloys containing rare earths |
| US11491257B2 (en) | 2010-07-02 | 2022-11-08 | University Of Florida Research Foundation, Inc. | Bioresorbable metal alloy and implants |
| CN101857936B (en) * | 2010-07-05 | 2012-05-23 | 重庆大学 | Method for preparing magnesium alloy |
| CN104195397B (en) * | 2014-09-10 | 2016-11-30 | 山西银光华盛镁业股份有限公司 | A kind of high-intensity thermal deformation resistant magnesium alloy and manufacture method thereof |
| WO2016118444A1 (en) | 2015-01-23 | 2016-07-28 | University Of Florida Research Foundation, Inc. | Radiation shielding and mitigating alloys, methods of manufacture thereof and articles comprising the same |
| RU2617072C2 (en) * | 2015-10-06 | 2017-04-19 | Федеральное государственное бюджетное учреждение науки Институт металлургии и материаловедения им. А.А. Байкова Российской академии наук (ИМЕТ РАН) | Castable magnesium alloy with rare earth metals |
| KR101876854B1 (en) * | 2016-08-12 | 2018-07-11 | 한국생산기술연구원 | Fe-Gd binary alloy for deoxidizing Fe alloy |
| CN106282675B (en) * | 2016-08-29 | 2017-12-15 | 北京工业大学 | A kind of technology of preparing of the high-strength rare earth-magnesium alloy board of inexpensive short route |
| CN106191599A (en) * | 2016-09-23 | 2016-12-07 | 闻喜县瑞格镁业有限公司 | A kind of high-strength high temperature-resistant creep resistance Dow metal and preparation method thereof |
| RU2682191C1 (en) * | 2018-05-23 | 2019-03-15 | федеральное государственное бюджетное образовательное учреждение высшего образования "Санкт-Петербургский горный университет" | Ligature for heat-resistant magnesium alloys |
| KR102054191B1 (en) * | 2019-09-26 | 2020-01-22 | 유앤아이 주식회사 | Biodegradable metal alloy |
| EP3888717A4 (en) * | 2018-11-30 | 2022-08-31 | U & I Corporation | Biodegradable metal alloy |
| CN110229984B (en) * | 2019-06-20 | 2020-08-04 | 上海交通大学 | High-strength Mg-Gd-Er-Y magnesium alloy and preparation method thereof |
| CN110964961A (en) * | 2019-12-31 | 2020-04-07 | 龙南龙钇重稀土科技股份有限公司 | High-strength high-corrosion-resistance magnesium alloy and preparation process thereof |
| CN113832371A (en) * | 2020-06-23 | 2021-12-24 | 宝山钢铁股份有限公司 | High-strength magnesium alloy extruded section and manufacturing method thereof |
| CN113088778B (en) * | 2021-04-02 | 2022-02-08 | 北京理工大学 | High-strength high-rigidity magnesium alloy and preparation method thereof |
| CN113564440A (en) * | 2021-08-02 | 2021-10-29 | 西安四方超轻材料有限公司 | High-performance easily-forged magnesium alloy material and preparation method thereof |
| CN115161504A (en) * | 2022-08-03 | 2022-10-11 | 重庆大学 | Design method for preparing high-concentration high-performance magnesium alloy based on Mg-Gd-Y and magnesium alloy |
| CN115300676A (en) * | 2022-08-08 | 2022-11-08 | 中南大学湘雅医院 | Medicine-carrying medical instrument and preparation method thereof |
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| SU460317A1 (en) * | 1973-05-03 | 1975-02-15 | Институт металлургии им.А.А.Байкова АН СССР | Magnesium based alloy |
| SU1010880A1 (en) * | 1981-09-25 | 1997-10-20 | М.Е. Дриц | Magnesium-base alloy |
| JPH07122114B2 (en) * | 1992-07-01 | 1995-12-25 | 三井金属鉱業株式会社 | High strength magnesium alloy containing gadolinium |
| JPH07138689A (en) * | 1993-11-09 | 1995-05-30 | Shiyoutarou Morozumi | Mg alloy excellent in high temperature strength |
| JP3664333B2 (en) * | 1996-03-29 | 2005-06-22 | 三井金属鉱業株式会社 | Hot forged product made of high strength magnesium alloy and its manufacturing method |
| JP3732600B2 (en) * | 1996-11-15 | 2006-01-05 | 株式会社セイタン | Yttrium-containing magnesium alloy |
| US7153374B2 (en) * | 2001-08-13 | 2006-12-26 | Honda Giken Kogyo Kabushiki Kaisha | Magnesium alloy |
| JP2004099941A (en) * | 2002-09-05 | 2004-04-02 | Japan Science & Technology Corp | Magnesium-base alloy and production method |
| WO2005052204A1 (en) * | 2003-11-26 | 2005-06-09 | Yoshihito Kawamura | High strength and high toughness magnesium alloy and method for production thereof |
| JP4840751B2 (en) * | 2004-06-30 | 2011-12-21 | 独立行政法人物質・材料研究機構 | High strength magnesium alloy and method for producing the same |
| JP4139841B2 (en) * | 2004-09-30 | 2008-08-27 | 能人 河村 | Casting and production method of magnesium alloy |
| CN100387743C (en) * | 2005-04-21 | 2008-05-14 | 上海交通大学 | High-strength heat-resisting magnesium alloy and its preparing method |
| JP4700488B2 (en) * | 2005-12-26 | 2011-06-15 | 本田技研工業株式会社 | Heat-resistant magnesium alloy |
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| JP5152775B2 (en) * | 2006-03-20 | 2013-02-27 | 株式会社神戸製鋼所 | Magnesium alloy material and method for producing the same |
| JP2008007793A (en) * | 2006-06-27 | 2008-01-17 | Nissan Motor Co Ltd | Sintered high-strength magnesium alloy, and its manufacturing method |
| JP5089945B2 (en) * | 2006-09-14 | 2012-12-05 | 国立大学法人 熊本大学 | High strength magnesium alloy with high corrosion resistance |
| JP2008291310A (en) * | 2007-05-24 | 2008-12-04 | Kumamoto Univ | Magnesium material production method |
| CN100469930C (en) * | 2007-07-04 | 2009-03-18 | 北京有色金属研究总院 | Creep resistance magnesium alloy and preparation method thereof |
| JP2009041066A (en) * | 2007-08-08 | 2009-02-26 | Hitachi Metals Ltd | Die-cast component of magnesium superior in heat resistance, cast compressor impeller and manufacturing method therefor |
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- 2006-09-13 GB GBGB0617970.9A patent/GB0617970D0/en not_active Ceased
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- 2007-09-12 BR BRPI0716895-0A patent/BRPI0716895A2/en not_active IP Right Cessation
- 2007-09-12 RU RU2009113576/02A patent/RU2450068C2/en active
- 2007-09-12 JP JP2009527892A patent/JP5309031B2/en active Active
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- 2007-09-12 WO PCT/GB2007/003491 patent/WO2008032087A2/en active Application Filing
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| WO2008032087A2 (en) | 2008-03-20 |
| RU2450068C2 (en) | 2012-05-10 |
| JP5309031B2 (en) | 2013-10-09 |
| CN101512029A (en) | 2009-08-19 |
| WO2008032087A3 (en) | 2008-05-22 |
| CA2663605A1 (en) | 2008-03-20 |
| KR20090055028A (en) | 2009-06-01 |
| BRPI0716895A2 (en) | 2013-10-22 |
| IL197400A0 (en) | 2009-12-24 |
| CN101512029B (en) | 2012-04-18 |
| RU2009113576A (en) | 2010-10-20 |
| GB0617970D0 (en) | 2006-10-18 |
| EP2074236B1 (en) | 2013-02-20 |
| IL197400A (en) | 2014-01-30 |
| TW200821392A (en) | 2008-05-16 |
| KR101350126B1 (en) | 2014-01-15 |
| EP2074236A2 (en) | 2009-07-01 |
| JP2010503767A (en) | 2010-02-04 |
| US20090175754A1 (en) | 2009-07-09 |
| TWI426137B (en) | 2014-02-11 |
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