WO2010038016A1 - Magnesium alloys containing rare earths - Google Patents
Magnesium alloys containing rare earths Download PDFInfo
- Publication number
- WO2010038016A1 WO2010038016A1 PCT/GB2009/002325 GB2009002325W WO2010038016A1 WO 2010038016 A1 WO2010038016 A1 WO 2010038016A1 GB 2009002325 W GB2009002325 W GB 2009002325W WO 2010038016 A1 WO2010038016 A1 WO 2010038016A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- weight
- alloy
- alloys
- less
- content
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
Definitions
- the present invention relates to magnesium alloys containing rare earths which possess improved processability and/or ductility, particularly when wrought, whilst retaining good corrosion resistance.
- Rare earths can be divided according their mass between Rare Earths (“RE” — defined herein as Y, La, Ce, Pr and Nd) and Heavy Rare Earths (“HRE” - defined herein as the elements with atomic numbers between 62 and 71 , i.e. Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu). Collectively they are often referred to as RE/HRE. It is known, for example from GB-A- 2095288, that the presence of RE/HRE provides magnesium alloys with good strength and creep resistance at elevated temperatures.
- RE Rare Earths
- HRE Heavy Rare Earths
- Magnesium - Yttrium - Neodymium - Heavy Rare Earth -Zirconium alloys are commercially available. Examples include those currently available under the trade marks Elektron WE43 and Elektron WE54 (hereinafter referred to as "WE43” and "WE54", respectively). WE43 and WE54 are designed for use from room temperature to 300° C. and it is known that these alloys can be used in both cast and wrought form. Their chemical composition, as defined by ASTM B 107/B 107M06, is shown below in Table 1 (taken from ASTM B107/B). These known WE43 and WE54 alloys will hereinafter be referred to collectively as "WE43 type alloys"
- WE43 type alloys typically include around 1% HRE, which can contain Sm, Eu, Gd, Tb, Dy, Ho, Er, Yb and Lu and other REs such as La, Ce and Pr (ref. King, Lyon, Savage. 59 th World Magnesium Conference, Montreal May 2002) .
- concentration of each of these individual elements is not specified in the literature, it merely being stated that "Other Rare Earths shall be principally heavy rare earths, for example Gd, Dy, Er, Yb" (Ref ASTM B107/B 107M06) , or there is a reference to "Nd and other heavy rare earths" (ref BSI 3116:2007).
- Mg-Y-Nd-HRE-Zr alloys such as WE43 type alloys were designed for applications at elevated temperatures (ref J Becker P 15-28 Magnesium alloys and applications proceedings 1998 edited BX Mordike).
- Strengthening precipitates containing Y/HRE and Nd are stable at elevated temperature and contribute to good tensile and creep performance. Whilst this strength and stability is of benefit for elevated temperature applications, this same characteristic can be of detriment during forming (wrought) operations. This is related to the alloys having limited formability and ductility. As a consequence, it is necessary to employ high processing temperatures, and low reduction rates (during hot forming operations) to minimise cracking. This adds to production cost and tends toward high scrap rates.
- magnesium-based alloys containing rare earths are described as having improved long-term strength and corrosion resistance by the essential incorporation thereinto of 0.1-2.5% by weight Zn and 0.01-0.05% by weight Mn.
- the ranges recited for Y, Gd, and Nd are broad and there is no recognition of the importance of the content of Gd in relation to the amount of Y in the alloy. Neither is there any recognition of the influence of other HREs. It is also apparent that the described alloy is intended for only cast applications and has been heat treated (T61).
- the present invention seeks to provide improved alloys over WE43 type alloys in terms of their processability and/or ductility, whilst at the same time retaining equally good corrosion resistance. This latter is achieved by careful control of both known corrosion-causing impurities, particularly iron, nickel and copper, and also those alloying element which have been found for the present alloys to be detrimental to their corrosion behaviour, such as Zn and Mn. There are various interactions between the alloying components which affect the corrosion behaviour of the alloy of the present invention, but that behaviour should be no worse than WE43 type alloys. Using the standard salt fog test of ASTM Bl 17 the alloys of the present invention should exhibit a corrosion rate of less than 30 Mpy.
- the alloys of the present invention when intended to be used as wrought alloys, should have the following characteristics as measured in their as-extruded state at room temperature under the conditions described in the examples below:
- alloys of the present invention may not need such high mechanical properties and lower values such as those defined by ASTM B107/B 107M-07, or even the following, may well be sufficient:
- the alloys of the present invention are also useful as casting alloys. Any subsequent processing of such casting alloys, such as heat treatment, will, of course, have a significant effect on the processability and ductility of the final material, and reduced tensile properties will generally only become manifest after such processing.
- Material in the F condition ie. as extruded without any further heat treatment, can contain particles of a size that can cause a reduction in tensile properties in the material, particularly during subsequent processing.
- the alloys of the present invention an improvement in processability and/or ductility becomes noticeable when the area percentage of such particles formed either in the cast alloy when in the T4 or T6 condition, or in the wrought material in the F or aged (T5) condition or after any other processing, which are readily detectable by optical microscopy, ie. having an average particle size in the range of about 1 to 15 ⁇ m, is less than 3%, and particularly less than 1.5%.
- optical microscopy ie. having an average particle size in the range of about 1 to 15 ⁇ m, is less than 3%, and particularly less than 1.5%.
- These optically resolvable particles tend to be brittle, and although their presence can be reduced through appropriated heat treatment, it is clearly preferable if their formation can be controlled by adjustment of the alloy's composition.
- the area percentage of particles having an average size greater than 1 and less than 7 ⁇ m is less than 3%.
- these particles does not necessarily depend on the specific amounts of Yb and/or Sm present. It has been found that for material in the F condition the presence of these particles is often related to the relative proportion of the RE/HRE to Gd, Dy and Er, and not only the amounts of Yb and Sm in the alloy. For many alloys the total of rare earths (excluding Y and Nd) other than Gd, Dy and Er should be less than 20%, preferably less than 13% and more preferably less than 5%, of the total weight of Gd, Dy and Er.
- the maximum content in the alloys of the present invention of the most unfavourable HREs, Yb and Sm does to a certain extent depend on the particular alloy composition, but generally tensile properties will not be reduced significantly for wrought material if the Yb content is not greater than 0.02% by weight and the Sm content is not greater than 0.04% by weight.
- the Yb content is less than 0.01% by weight and the Sm content is less than 0.02% by weight.
- Sm 0-0.04% by weight, optionally rare earths and heavy rare earths other than Y, Nd, Gd, Dy, Er, Yb and
- a magnesium alloy consisting of:
- Zn + Mn ⁇ 0.11 % by weight, optionally rare earths and heavy rare earths other than Y, Nd, Gd, Dy and Er in a total amount of up to 20 % by weight, and the balance being magnesium and incidental impurities up to a total of 0.3% by weight, wherein the total content of Gd, Dy and Er is in the range of 0.3 - 12 % by weight, and wherein when the alloy is in the T4 or T6 condition the area percentage of any precipitated particles having an average particle size of between 1 and 15 ⁇ m is less than 3%.
- the cast alloy exhibits a corrosion rate as measured according to ASTM Bl 17 of less than 30 Mpy.
- Fig 1 is a graph showing the effect of alloying elements on the recrystallisation temperature of magnesium (taken from the latter mentioned Rokhlin 2003 reference),
- Figs 2 A and 2C show the microstructures of two samples made from WE43 type alloys after extrusion at 45O 0 C, the composition of the alloys being those of Sample Ia and Sample Ib of Table 3 below, respectively,
- Figs 2B and 2D show microstructures of two samples made from magnesium alloys of the present invention after extrusion at 45O 0 C, the composition of the alloys being those of Sample 3d and Sample 3a of Table 3 below, respectively,
- Figure 3 shows the microstructure of a sample of commercial wrought WE43 alloy which has failed under tensile load revealing in two areas cracks which are associated with the presence of brittle particles therein,
- Figs 4A and 4B are micrographs of two samples of sand cast alloys in the T4 condition, their compositions being Sample C and Sample D of Table 3 below, respectively.
- Recrystallisation This is the ability to form new unstrained grains and is beneficial in restoring ductility to material, which has been strained (for example, but not limited to, extrusion, rolling and drawing). Recrystallisation allows material to be re-strained to achieve further deformation. Recrystallisation is often achieved by heating the alloy (annealing) between processing steps.
- the temperature at which recrystallisation takes place or the time taken to complete recrystallisation can be lowered then the number and/or time of elevated temperature annealing steps can be reduced, and the forming (processing) of the material can be improved.
- particles in these alloys can arise from the interactions of any of their constituent elements, of particular interest to this invention are those particles which are formed from HRE/RE constituents.
- WE43 type alloys typically contain 1% HRE, which can consist of Gd, Dy, Er, Yb, Eu, Tb, Ho and Lu and other REs such as La, Ce and Pr. It has been discovered that by removing selective RE and HRE from a WE43 type alloy, without reducing the overall HRE content of the alloy, the occurrence and size of such particles is reduced.
- the alloy's ductility can be improved and its recrystallisation temperature and/or recrystallisation time may be reduced, without significantly adversely affecting the alloy's tensile and corrosion properties, thus offering the opportunity to improve the forming processes applied to the alloy.
- Y and Nd are the elements which improve the strength of the alloys to which the present invention relates by the mechanism of precipitation hardening. This relies on the fact that these alloy constituents are in a state of supersaturation and can subsequently be brought out of solution in a controlled manner during ageing (typically at temperatures in the range 200-250°C).
- the precipitates desired for strength are small in size and these strengthening precipitates can not be resolved by optical microscopy.
- additional precipitates are also generated which are coarse and readily observed by optical microscopy as particles. These are usually rich in Nd and have an average particle size of less than 15 ⁇ m and generally up to about 10 ⁇ m (see accompanying Fig 2B).
- a particle rich in Nd has a percentage composition of Nd greater than the percentage composition of any other element in the particle.
- the present invention seeks to reduce the occurrence of such coarse particles by controlling the alloying components which have been found to cause these particles to be formed. In the course of examining the causation of these undesirable particles an unexpected link with the solubility of these alloying elements has been found.
- WE43 type alloys Another notable feature of WE43 type alloys is their resistance to corrosion. It is well known that general corrosion of magnesium alloys is affected by contaminants such as iron, nickel, copper and cobalt (J Hillis, Corrosion Ch 7.2 p470. Magnesium Technology, 2006 Edited Mordike). This is due to the large difference in electro potential between these elements and magnesium. Ia corrosive environments, micro galvanic cells are produced, which lead to corrosion.
- the corrosion performance of the present alloys can be improved; for some by a factor of approximately four. This is found to occur without reducing the overall total RE/HRE content of these alloys.
- the present invention achieves the above described benefits by the control of both unfavourable HREs/REs, particularly Yb, and favourable HREs, namely Gd and/or Dy and/or Er.
- inventive alloys become most apparent when the alloy is wrought, eg by extrusion. Furthermore although the mechanical properties of the alloys of the present invention can be favourably altered by known heat treatments, the improved ductility achieved by the described control of the alloy's composition can be attained without the need for such heat treatments.
- inventive alloys can be used in similar applications to those in which WE43 type alloys can be used. They can be cast and/or heat treated and/or wrought, as well as being suitable as base alloys for metal matrix composites.
- the content of Y in the inventive alloys is 3.5 - 4.5% by weight, more preferably 3.7 - 4.3% by weight. Keeping the content of Y within these preferred ranges ensures that the consistency of properties, e.g. scatter during tensile testing, is maintained. Too low a Y content leads to a reduction in strength, whilst too high a Y content leads to a fall in ductility.
- the content of Nd in the alloys is preferably 1.5 - 3.5% by weight, more preferably 2.0 - 3.0% by weight, most preferably 2.0 - 2.5% by weight.
- the strength of the alloy starts to decrease significantly.
- the content of Nd is raised above 4.0% by weight, the ductility of the alloy is deteriorated due to limited solubility of Nd in Mg.
- the essential desirable HREs, Gd, Dy and Er there should be at least 0.3% in total for their presence to have a significant effect on the processability and/or ductility of the alloy.
- each may be present in an amount up to 5.5% by weight, but their preferred range depends on their solubility in the particular alloy, since as the quantity and size of precipitated particles in the alloy increases so the alloy's ductility falls.
- the relative amount of these desirable HREs compared to other HREs is important, since it has been found that for undesirable HREs, such as Yb and Sm, their effect on particularly the alloy's ductility is disproportionate to their content.
- the total content of Gd, Dy and Er in the inventive alloys is preferably in the range of 0.4 - 4.0 by weight, and more preferably from 0.5 up to 1.0% by weight., especially up to but less than 0.6% by weight.
- the total content of Nd, Gd, Dy and Er in the alloy is preferably in the range of 2.0 - 5.5% by weight. Within this range, maintenance of good ductility can be ensured.
- rare earths and heavy rare earths other than Y, Nd, Gd, Dy, Er, Yb and Sm can be present in a total amount of up to 0.5 % by weight.
- rare earths and heavy rare earths other than Y, Nd, Gd, Dy and Er can be present in a total amount of up to 20 %, and preferably up to 5% by weight. It is preferred that the total content of rare earths (excluding Y and Nd) other than Gd, Dy and Er is less than 5% of the total weight of Gd, Dy and Er.
- the inventive magnesium alloy includes Gd and Dy, especially solely Gd.
- zirconium has a significant benefit of reducing the grain size of magnesium alloys, especially of the pre-extruded material, which improves the ductility of the alloy. It has further been found that impurities of iron and nickel should be controlled. This can be achieved by the addition of zirconium and aluminium which combine with iron and nickel to form an insoluble compound. This compound is precipitated in the melting crucible and settles prior to casting [Emley et al, Principles of Magnesium Technology. Pergamon Press 1966, p. 126ff; Foerster, US 3,869,281, 1975]. Thus Zr and Al can contribute to improved corrosion resistance.
- the content of Zr should be at least 0.05% by weight while the content of Al should be less than 0.3% by weight in the final alloy, and preferably no more than 0.2% by weight.
- Zr is near its lowest level, namely 0.05 % by weight, corrosion test results tend to become erratic.
- the inventive magnesium alloy can include less than 0.2% and preferably less than 0.02 % by weight of Li, but should not contain more than 0.11% in total of Zn and Mn.
- the total content of impurities in the alloy should be less than 0.3% by weight, and preferably less that 0.2 % by weight.
- the following maximum impurity levels should be preserved:
- inventive alloy comprise at least 91% by weight Mg.
- the billet was machined to nominally 75mm diameter and 150-250 mm length in order to prepare the sample for extrusion.
- Extrusion was carried out on a hydraulic press.
- the product from the 75mm billet was round bar section, with an available section of 3.2 to 25 mm diameter, but more typically 9.5mm.
- the extruded section was used for evaluation.
- Cast material was produced by melting in the same manner described previously, but here the molten alloy was poured into sand moulds to produce castings typically 200mm*200mm*25mm with no subsequent extrusion or forging operations.
- the material was heat treated at 525C to solutionise its structure, cooled to room temperature (known as T4 treatment) and subsequently aged at 250C for 16 hours. This material and total heat treatment is referred to herein as "Sand cast T6". It should be noted that, unlike the other samples, Sample Ia and Sample A additionally contain 0.13% Li.
- Table 3 below, which is divided into sections a and b, summarises the chemical compositions, corrosion rates and room temperature tensile properties of the F condition extruded and the Sand cast T6 alloys tested.
- Samples Ia-Ih and Sample A are comparative examples of WE43 type alloys. Melts were produced to generate tensile data and for metallo graphic analysis.
- YS is the yield strength or yield point of the material and is the stress at which material strain changes from elastic deformation to plastic deformation, causing the sample to defo ⁇ n permanently.
- UTS means Ultimate Tensile Strength which is the maximum stress which the material could withstand before breaking.
- "Elong” stands for elongation at fracture.
- Table 3 a sets out the data for the extruded samples whilst Table 3b shows the equivalent results for the cast samples.
- inventive changes in the composition of the alloys were not seriously detrimental to tensile properties in terms of strength, but in the case of ductility as measured by elongation, a noticeable improvement was observed where the HRE component of the alloys was rich in Gd and/or Dy and/or Er.
- Table 3b shows similar results for cast material in which Samples A and C are WE43 type alloys and Samples B and D are within the present invention.
- Table 4 sets out the estimated area and mean size data of particles found in a selection of alloys.
- the technique used was optical microscopy using commercially available software to analyse particle area and size by difference in colouration of particles. This technique does not give an absolute value, but does give a good estimation which was compared with physical measurement of random particles.
- Table 4 clearly illustrates a reduction in the number of detectable particles in the alloys of this invention, which particles are likely to be brittle.
- FIG. 2 shows microstructures of two comparative Samples Ia (FIG. 2A) and Ib (FIG 2C) and two inventive samples 3d (FIG. 2B) and 3a (FIG 2D) after extrusion at 450 0 C.
- Ia comparative Samples Ia
- Ib comparative Samples Ib
- Ib inventive samples 3d
- FIG. 2D 3a
- the inventive magnesium alloy has significantly fewer precipitates and a slightly larger grain size after extrusion. Further investigation revealed that after several deformation steps and the respective intermediate heat treatments there were significantly fewer and smaller precipitates in sample 3d and that the grain size of sample 3d is still slightly larger than for comparative Sample Ia which was processed in exactly the same way.
- inventive magnesium alloys are less sensitive to temperature variations.
- the range between uniform elongation and elongation at fracture is more uniform compared to conventional magnesium alloys.
- inventive alloys tested softened at a lower annealing temperature than conventional alloys and thus ductility was maintained at a more uniform level.
- FIGS 2A and 2C are micrographs showing the area percentage of clearly visible particles in samples of two of the WE43 type alloys whose analyses are set out in Table 3 a. It will be noted that the area percentage is greater than 3%. The presence of such an amount of large particles has the effect of endowing those alloys with relatively poor ductility.
- Figures 2B and 2D show for samples of magnesium alloys of the present invention area percentages of the large particles less than 1.5%, which correlates with significantly improved ductility.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Powder Metallurgy (AREA)
- Forging (AREA)
- Extrusion Of Metal (AREA)
- Battery Electrode And Active Subsutance (AREA)
Abstract
Description
Claims
Priority Applications (13)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AU2009299656A AU2009299656B2 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
CA2738973A CA2738973C (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
DK09759968.2T DK2350330T3 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
CN200980138669.4A CN102187004B (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
MX2011003293A MX2011003293A (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths. |
BRPI0919523-8A BRPI0919523B1 (en) | 2008-09-30 | 2009-09-30 | MAGNESIUM ALLOYS CONTAINING RARE EARTH |
ES09759968.2T ES2447592T3 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
PL09759968T PL2350330T3 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
JP2011528421A JP5814122B2 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloy containing rare earth elements |
US13/121,588 US9017604B2 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
EP09759968.2A EP2350330B1 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
RU2011112054/02A RU2513323C2 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloy, containing rare earth metals |
IL211949A IL211949A (en) | 2008-09-30 | 2011-03-27 | Magnesium alloys containing rare earths |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
GBGB0817893.1A GB0817893D0 (en) | 2008-09-30 | 2008-09-30 | Magnesium alloys containing rare earths |
GB0817893.1 | 2008-09-30 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2010038016A1 true WO2010038016A1 (en) | 2010-04-08 |
Family
ID=40019809
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/GB2009/002325 WO2010038016A1 (en) | 2008-09-30 | 2009-09-30 | Magnesium alloys containing rare earths |
Country Status (15)
Country | Link |
---|---|
US (1) | US9017604B2 (en) |
EP (1) | EP2350330B1 (en) |
JP (1) | JP5814122B2 (en) |
CN (1) | CN102187004B (en) |
AU (1) | AU2009299656B2 (en) |
BR (1) | BRPI0919523B1 (en) |
CA (1) | CA2738973C (en) |
DK (1) | DK2350330T3 (en) |
ES (1) | ES2447592T3 (en) |
GB (1) | GB0817893D0 (en) |
IL (1) | IL211949A (en) |
MX (1) | MX2011003293A (en) |
PL (1) | PL2350330T3 (en) |
RU (1) | RU2513323C2 (en) |
WO (1) | WO2010038016A1 (en) |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102628134A (en) * | 2011-02-01 | 2012-08-08 | 亥姆霍兹中心盖斯特哈赫特材料及海岸研究中心有限公司 | Single-phase solid solution cast or wrought magnesium alloys |
JP2014533967A (en) * | 2011-09-06 | 2014-12-18 | シンテリックス アーゲー | Method for producing a medical implant from a magnesium alloy |
US20150362006A1 (en) * | 2009-05-29 | 2015-12-17 | Sumitomo Electric Industries, Ltd. | Linear object and bolt, including a magnesium alloy |
DE102015101264A1 (en) | 2015-01-28 | 2016-07-28 | Limedion GmbH | Biodegradable alloy and its production and use, in particular for the production of stents and other implants |
WO2016123181A1 (en) * | 2015-01-28 | 2016-08-04 | Medtronic Vascular Inc. | Magnesium and rare earth element alloy |
EP3097217A4 (en) * | 2014-01-23 | 2017-09-20 | Dead Sea Magnesium Ltd. | High performance creep resistant magnesium alloys |
RU2642254C2 (en) * | 2011-08-15 | 2018-01-24 | Меко Лазерштраль-Материальбеарбайтунген Е.К. | Dissolving stents containing magnesium alloys |
US9920402B2 (en) | 2010-03-25 | 2018-03-20 | Magnesium Elektron Limited | Magnesium alloys containing heavy rare earths |
WO2018130816A1 (en) * | 2017-01-16 | 2018-07-19 | Magnesium Elektron Limited | Corrodible downhole article |
RU2687359C1 (en) * | 2018-11-23 | 2019-05-13 | Федеральное государственное автономное образовательное учреждение высшего образования "Национальный исследовательский технологический университет "МИСиС" | Magnesium casting alloy |
US10329643B2 (en) | 2014-07-28 | 2019-06-25 | Magnesium Elektron Limited | Corrodible downhole article |
US11167343B2 (en) | 2014-02-21 | 2021-11-09 | Terves, Llc | Galvanically-active in situ formed particles for controlled rate dissolving tools |
US11365164B2 (en) | 2014-02-21 | 2022-06-21 | Terves, Llc | Fluid activated disintegrating metal system |
RU2781338C1 (en) * | 2021-09-07 | 2022-10-11 | федеральное государственное бюджетное образовательное учреждение высшего образования "Тольяттинский государственный университет" (ТГУ) | Fire-resistant magnesium casting alloy |
US11649526B2 (en) | 2017-07-27 | 2023-05-16 | Terves, Llc | Degradable metal matrix composite |
US12018356B2 (en) | 2014-04-18 | 2024-06-25 | Terves Inc. | Galvanically-active in situ formed particles for controlled rate dissolving tools |
Families Citing this family (36)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2213314B1 (en) * | 2009-01-30 | 2016-03-23 | Biotronik VI Patent AG | Implant with a base body of a biocorrodible magnesium alloy |
JP5952803B2 (en) * | 2010-03-25 | 2016-07-13 | バイオトロニック アクチェンゲゼルシャフト | Implants made from biodegradable magnesium alloys |
CN103205591B (en) * | 2012-10-24 | 2016-12-28 | 哈尔滨东安发动机(集团)有限公司 | MgYNdZr alloy method of refining |
CN103498088B (en) * | 2013-10-17 | 2016-06-01 | 中国科学院长春应用化学研究所 | A kind of magnesium-rare earth and its preparation method |
RU2554269C1 (en) * | 2014-03-03 | 2015-06-27 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Magnesium-based alloy and product made from it |
CN104278185A (en) * | 2014-11-03 | 2015-01-14 | 北京汽车股份有限公司 | High-strength and high-modulus rare-earth magnesium matrix composite material containing SiC particles for automobiles |
CN104313441B (en) * | 2014-11-03 | 2018-01-16 | 北京汽车股份有限公司 | A kind of rare earth and magnesium-based composite of high-modulus containing SiC particulate |
RU2562190C1 (en) * | 2014-11-10 | 2015-09-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Magnesium-based alloy |
RU2578275C1 (en) * | 2014-12-22 | 2016-03-27 | Юлия Алексеевна Щепочкина | Magnesium-based alloy |
CN104451474B (en) * | 2014-12-25 | 2016-06-29 | 哈尔滨工业大学 | A kind of preparation method of the Cf/Mg composite of high interfacial strength |
CN105033499B (en) * | 2015-08-26 | 2017-03-29 | 南昌航空大学 | A kind of heat resistance magnesium alloy solder for magnesium-rare earth soldering and preparation method thereof |
CN105154736B (en) * | 2015-10-23 | 2017-06-16 | 中国兵器工业第五九研究所 | A kind of heat resistance casting magnesium alloy and preparation method thereof |
US10738561B2 (en) * | 2015-12-25 | 2020-08-11 | Kureha Corporation | Stock shape for downhole tool component, downhole tool component, and downhole tool |
CN107586911B (en) * | 2016-07-08 | 2019-11-05 | 北京机科国创轻量化科学研究院有限公司 | The novel vermiculizer of vermicular cast iron |
CN106048353A (en) * | 2016-08-23 | 2016-10-26 | 肖旅 | High-plasticity magnesium alloy for controllable reaction with water and manufacture method of magnesium alloy component |
CN106498252B (en) * | 2016-10-27 | 2018-04-13 | 江苏理工学院 | A kind of high-strength magnesium neodymium zinc zirconium lithium alloy and preparation method thereof |
CN107058833A (en) * | 2016-11-08 | 2017-08-18 | 中航装甲科技有限公司 | A kind of graphene composite armour material and preparation method thereof |
CN106756370A (en) | 2016-12-10 | 2017-05-31 | 哈尔滨工业大学 | A kind of anti-flaming Mg Gd Y Zn Zr alloys of high-strength anticorrosion and preparation method thereof |
GB201700714D0 (en) * | 2017-01-16 | 2017-03-01 | Magnesium Elektron Ltd | Corrodible downhole article |
CN107245619B (en) * | 2017-03-03 | 2018-08-10 | 中南大学 | A kind of strong high temperature resistant magnesium alloy of superelevation |
CN107130158B (en) * | 2017-04-20 | 2018-09-21 | 赣南师范大学 | A kind of high heat conduction magnesium-rare earth and preparation method thereof |
CN106929727B (en) * | 2017-04-20 | 2018-09-21 | 赣南师范大学 | A kind of high capability of electromagnetic shielding magnesium alloy and preparation method thereof |
CN107227421B (en) * | 2017-05-11 | 2019-04-09 | 江苏理工学院 | Magnesium lithium alloy and preparation method thereof |
CN106978557A (en) * | 2017-05-11 | 2017-07-25 | 江苏理工学院 | A kind of magnesium lithium alloy and preparation method thereof |
CN107201473A (en) * | 2017-06-07 | 2017-09-26 | 深圳市威富通讯技术有限公司 | A kind of magnesium alloy and preparation method thereof, cavity body filter |
CN107502802A (en) * | 2017-09-19 | 2017-12-22 | 西安理工大学 | Instrument magnesium alloy and preparation method thereof is temporarily blocked up in a kind of oil-gas mining |
CN107858616B (en) * | 2017-12-12 | 2019-08-27 | 重庆市科学技术研究院 | A kind of high-strength and high-plasticity Mg-Gd-Y-Zn-Nd-Zr cast magnesium alloy and preparation method thereof |
CN108774703B (en) * | 2018-08-23 | 2020-05-19 | 中国科学院长春应用化学研究所 | Li-containing light high-strength magnesium alloy and preparation method thereof |
KR102178806B1 (en) * | 2018-09-28 | 2020-11-13 | 주식회사 포스코 | Magnesium alloy sheet and method for manufacturing the same |
CN109943760B (en) * | 2019-05-15 | 2021-04-02 | 湖南科技大学 | High-strength high-plasticity rare earth magnesium alloy and preparation method thereof |
CN110964959A (en) * | 2019-12-20 | 2020-04-07 | 佛山科学技术学院 | High-strength magnesium-lithium alloy |
CN112195421B (en) * | 2020-09-07 | 2022-02-18 | 北京工业大学 | Island-shaped beta in rare earth magnesium-lithium alloy1Method for separating out nanophase |
CN113106275B (en) * | 2021-04-09 | 2021-11-16 | 河北大有镁业有限责任公司 | Continuous production method of high-quality multi-element rare earth magnesium alloy with controllable end point component |
CN113444946B (en) * | 2021-05-17 | 2022-02-11 | 中北大学 | High-strength and high-toughness rare earth magnesium alloy and treatment method thereof |
CN113528880A (en) * | 2021-06-08 | 2021-10-22 | 上海航天精密机械研究所 | Grain refiner for rare earth magnesium alloy, preparation method and method for preparing rare earth magnesium alloy by using grain refiner |
CN113528915B (en) * | 2021-07-09 | 2022-02-11 | 青岛理工大学 | Impact-resistant high-strength heat-resistant magnesium rare earth alloy material |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2095288A (en) * | 1981-03-25 | 1982-09-29 | Magnesium Elektron Ltd | Magnesium alloys |
JPH09104955A (en) * | 1995-10-07 | 1997-04-22 | Kobe Steel Ltd | Method for heat treating magnesinum-yttrium-rare earth-zirconium base alloy |
JPH09263871A (en) * | 1996-03-29 | 1997-10-07 | Mitsui Mining & Smelting Co Ltd | Hot forged product made of high strength magnesium alloy and its production |
JPH10147830A (en) * | 1996-11-15 | 1998-06-02 | Tokyo Seitankoushiyo:Kk | Yttrium-containing magnesium alloy |
US20020104761A1 (en) * | 1997-03-26 | 2002-08-08 | Birss Viola I. | Coated substrate and process for production thereof |
CN101008060A (en) * | 2006-11-30 | 2007-08-01 | 中国科学院长春应用化学研究所 | Heat-proof magnesium-base rare earth alloy and its preparation method |
CN101078080A (en) * | 2007-07-04 | 2007-11-28 | 北京有色金属研究总院 | Creep resistance magnesium alloy and preparation method thereof |
WO2008032087A2 (en) * | 2006-09-13 | 2008-03-20 | Magnesium Elektron Limited | Magnesium gadolinium alloys |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SU1360223A1 (en) * | 1985-09-24 | 1994-10-15 | В.А. Блохина | Magnesium-based alloys |
FR2688233B1 (en) | 1992-03-05 | 1994-04-15 | Pechiney Electrometallurgie | MAGNESIUM ALLOYS DEVELOPED BY RAPID SOLIDIFICATION HAVING HIGH HOT MECHANICAL RESISTANCE. |
US6495267B1 (en) * | 2001-10-04 | 2002-12-17 | Briggs & Stratton Corporation | Anodized magnesium or magnesium alloy piston and method for manufacturing the same |
AUPS311202A0 (en) * | 2002-06-21 | 2002-07-18 | Cast Centre Pty Ltd | Creep resistant magnesium alloy |
JP3852769B2 (en) * | 2002-11-06 | 2006-12-06 | 三菱製鋼株式会社 | Room temperature formable magnesium alloy with excellent corrosion resistance |
-
2008
- 2008-09-30 GB GBGB0817893.1A patent/GB0817893D0/en not_active Ceased
-
2009
- 2009-09-30 BR BRPI0919523-8A patent/BRPI0919523B1/en active IP Right Grant
- 2009-09-30 CA CA2738973A patent/CA2738973C/en active Active
- 2009-09-30 EP EP09759968.2A patent/EP2350330B1/en active Active
- 2009-09-30 MX MX2011003293A patent/MX2011003293A/en active IP Right Grant
- 2009-09-30 RU RU2011112054/02A patent/RU2513323C2/en active
- 2009-09-30 WO PCT/GB2009/002325 patent/WO2010038016A1/en active Application Filing
- 2009-09-30 US US13/121,588 patent/US9017604B2/en active Active
- 2009-09-30 PL PL09759968T patent/PL2350330T3/en unknown
- 2009-09-30 DK DK09759968.2T patent/DK2350330T3/en active
- 2009-09-30 JP JP2011528421A patent/JP5814122B2/en active Active
- 2009-09-30 AU AU2009299656A patent/AU2009299656B2/en active Active
- 2009-09-30 CN CN200980138669.4A patent/CN102187004B/en active Active
- 2009-09-30 ES ES09759968.2T patent/ES2447592T3/en active Active
-
2011
- 2011-03-27 IL IL211949A patent/IL211949A/en active IP Right Grant
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2095288A (en) * | 1981-03-25 | 1982-09-29 | Magnesium Elektron Ltd | Magnesium alloys |
JPH09104955A (en) * | 1995-10-07 | 1997-04-22 | Kobe Steel Ltd | Method for heat treating magnesinum-yttrium-rare earth-zirconium base alloy |
JPH09263871A (en) * | 1996-03-29 | 1997-10-07 | Mitsui Mining & Smelting Co Ltd | Hot forged product made of high strength magnesium alloy and its production |
JPH10147830A (en) * | 1996-11-15 | 1998-06-02 | Tokyo Seitankoushiyo:Kk | Yttrium-containing magnesium alloy |
US20020104761A1 (en) * | 1997-03-26 | 2002-08-08 | Birss Viola I. | Coated substrate and process for production thereof |
WO2008032087A2 (en) * | 2006-09-13 | 2008-03-20 | Magnesium Elektron Limited | Magnesium gadolinium alloys |
CN101008060A (en) * | 2006-11-30 | 2007-08-01 | 中国科学院长春应用化学研究所 | Heat-proof magnesium-base rare earth alloy and its preparation method |
CN101078080A (en) * | 2007-07-04 | 2007-11-28 | 北京有色金属研究总院 | Creep resistance magnesium alloy and preparation method thereof |
Non-Patent Citations (5)
Title |
---|
J HILLIS: "Corrosion", 2006, MAGNESIUM TECHNOLOGY, pages: 470 |
LL.ROKHLIN: "Magnesium alloys containing RE metals", 2003, TAYLOR & FRANCIS, pages: 205 |
MARROW T J ET AL: "Environment-assisted cracking of cast WE43-T6 magnesium", MATERIALS SCIENCE AND ENGINEERING A: STRUCTURAL MATERIALS:PROPERTIES, MICROSTRUCTURE & PROCESSING, LAUSANNE, CH, vol. 387-389, 15 December 2004 (2004-12-15), pages 419 - 423, XP004664223, ISSN: 0921-5093 * |
ZHANG, KUI; LI, XING-GANG; LI, YONG-JUN; MA, MING-LONG: "Effect of Gd content on microstructure and mechanical properties of Mg- Y -RE- Zr alloys", TRANSACTIONS OF NONFERROUS METALS SOCIETY OF CHINA, vol. 18, 5 September 2008 (2008-09-05), pages 12 - 16, XP008118966, ISSN: 1003-6326 * |
ZHAO, XIN; ZHANG, KUI; LI, XINGGANG; LI, YONGJUN; HE, QINGBIAO; SUN, JIANFENG: "Hot deformation behavior of Mg- Y - Nd - Gd -Zr alloy", XIYOU JINSHU (CHINESE JOURNAL OF RARE METALS), vol. 32, no. 3, June 2008 (2008-06-01), pages 263 - 268, XP008118967, ISSN: 0258-7076 * |
Cited By (24)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20150362006A1 (en) * | 2009-05-29 | 2015-12-17 | Sumitomo Electric Industries, Ltd. | Linear object and bolt, including a magnesium alloy |
US9920402B2 (en) | 2010-03-25 | 2018-03-20 | Magnesium Elektron Limited | Magnesium alloys containing heavy rare earths |
CN102628134A (en) * | 2011-02-01 | 2012-08-08 | 亥姆霍兹中心盖斯特哈赫特材料及海岸研究中心有限公司 | Single-phase solid solution cast or wrought magnesium alloys |
RU2642254C2 (en) * | 2011-08-15 | 2018-01-24 | Меко Лазерштраль-Материальбеарбайтунген Е.К. | Dissolving stents containing magnesium alloys |
JP2014533967A (en) * | 2011-09-06 | 2014-12-18 | シンテリックス アーゲー | Method for producing a medical implant from a magnesium alloy |
EP3097217A4 (en) * | 2014-01-23 | 2017-09-20 | Dead Sea Magnesium Ltd. | High performance creep resistant magnesium alloys |
US11613952B2 (en) | 2014-02-21 | 2023-03-28 | Terves, Llc | Fluid activated disintegrating metal system |
US11365164B2 (en) | 2014-02-21 | 2022-06-21 | Terves, Llc | Fluid activated disintegrating metal system |
US11167343B2 (en) | 2014-02-21 | 2021-11-09 | Terves, Llc | Galvanically-active in situ formed particles for controlled rate dissolving tools |
US12018356B2 (en) | 2014-04-18 | 2024-06-25 | Terves Inc. | Galvanically-active in situ formed particles for controlled rate dissolving tools |
US10329643B2 (en) | 2014-07-28 | 2019-06-25 | Magnesium Elektron Limited | Corrodible downhole article |
US10337086B2 (en) | 2014-07-28 | 2019-07-02 | Magnesium Elektron Limited | Corrodible downhole article |
WO2016123181A1 (en) * | 2015-01-28 | 2016-08-04 | Medtronic Vascular Inc. | Magnesium and rare earth element alloy |
DE102015101264A1 (en) | 2015-01-28 | 2016-07-28 | Limedion GmbH | Biodegradable alloy and its production and use, in particular for the production of stents and other implants |
WO2018130816A1 (en) * | 2017-01-16 | 2018-07-19 | Magnesium Elektron Limited | Corrodible downhole article |
RU2756521C2 (en) * | 2017-01-16 | 2021-10-01 | Магнезиум Электрон Лимитед | Corrosion-prone borehole product |
US10266923B2 (en) | 2017-01-16 | 2019-04-23 | Magnesium Elektron Limited | Corrodible downhole article |
CN109906304A (en) * | 2017-01-16 | 2019-06-18 | 镁电子有限公司 | Corrodible underground product |
CN109906304B (en) * | 2017-01-16 | 2021-07-23 | 镁电子有限公司 | Corrodible downhole article |
US11649526B2 (en) | 2017-07-27 | 2023-05-16 | Terves, Llc | Degradable metal matrix composite |
US11898223B2 (en) | 2017-07-27 | 2024-02-13 | Terves, Llc | Degradable metal matrix composite |
RU2687359C1 (en) * | 2018-11-23 | 2019-05-13 | Федеральное государственное автономное образовательное учреждение высшего образования "Национальный исследовательский технологический университет "МИСиС" | Magnesium casting alloy |
RU2781338C1 (en) * | 2021-09-07 | 2022-10-11 | федеральное государственное бюджетное образовательное учреждение высшего образования "Тольяттинский государственный университет" (ТГУ) | Fire-resistant magnesium casting alloy |
US12031400B2 (en) | 2023-02-15 | 2024-07-09 | Terves, Llc | Fluid activated disintegrating metal system |
Also Published As
Publication number | Publication date |
---|---|
MX2011003293A (en) | 2011-08-03 |
CA2738973A1 (en) | 2010-04-08 |
AU2009299656A1 (en) | 2010-04-08 |
CN102187004A (en) | 2011-09-14 |
US9017604B2 (en) | 2015-04-28 |
IL211949A (en) | 2015-07-30 |
BRPI0919523B1 (en) | 2020-05-26 |
CN102187004B (en) | 2014-05-07 |
RU2513323C2 (en) | 2014-04-20 |
EP2350330B1 (en) | 2013-11-27 |
EP2350330A1 (en) | 2011-08-03 |
PL2350330T3 (en) | 2014-04-30 |
BRPI0919523A2 (en) | 2016-09-20 |
US20110229365A1 (en) | 2011-09-22 |
JP2012504186A (en) | 2012-02-16 |
IL211949A0 (en) | 2011-06-30 |
CA2738973C (en) | 2017-08-29 |
JP5814122B2 (en) | 2015-11-17 |
DK2350330T3 (en) | 2014-02-03 |
ES2447592T3 (en) | 2014-03-12 |
AU2009299656B2 (en) | 2014-03-06 |
RU2011112054A (en) | 2012-11-10 |
GB0817893D0 (en) | 2008-11-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2350330B1 (en) | Magnesium alloys containing rare earths | |
US7108042B2 (en) | Aluminum diecasting alloy | |
US9074269B2 (en) | Magnesium alloy | |
EP2664687B1 (en) | Improved free-machining wrought aluminium alloy product and manufacturing process thereof | |
EP1897962B1 (en) | Creep resistant magnesium alloy with improved ductility and fracture toughness for gravity casting applications | |
WO2010122960A1 (en) | High-strength copper alloy | |
JP5237801B2 (en) | Doped iridium with improved high temperature properties | |
WO2016034857A1 (en) | A casting al-mg-zn-si based aluminium alloy for improved mechanical performance | |
CN102628134A (en) | Single-phase solid solution cast or wrought magnesium alloys | |
JP2010018875A (en) | High strength aluminum alloy, method for producing high strength aluminum alloy casting, and method for producing high strength aluminum alloy member | |
WO2009136552A1 (en) | Brass alloy powder, brass alloy extruded material and method for producing the brass alloy extruded material | |
JP5215710B2 (en) | Magnesium alloy with excellent creep characteristics at high temperature and method for producing the same | |
Zhihao et al. | Effect of Mn on microstructures and mechanical properties of Al-Mg-Si-Cu-Cr-V alloy. | |
JP4145242B2 (en) | Aluminum alloy for casting, casting made of aluminum alloy and method for producing casting made of aluminum alloy | |
WO2016132994A1 (en) | Aluminum alloy worked material, and manufacturing method thereof | |
US20200354818A1 (en) | High Strength Microalloyed Magnesium Alloy | |
JP5575028B2 (en) | High strength aluminum alloy, high strength aluminum alloy casting manufacturing method and high strength aluminum alloy member manufacturing method | |
US8016957B2 (en) | Magnesium grain-refining using titanium | |
CN102703786B (en) | Heat-resisting anti-corrosion magnesium alloy for automobile engine cylinder | |
WO2023080056A1 (en) | Magnesium-based alloy extension material | |
KR20230171947A (en) | Oxidation-resistant Al-Mg high-strength die casting alloy | |
JP6638193B2 (en) | Aluminum alloy processing material and method of manufacturing the same | |
EP4101941A1 (en) | Aluminium-silicon casting alloy, and castings made from said alloy |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 200980138669.4 Country of ref document: CN |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 09759968 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2009299656 Country of ref document: AU |
|
WWE | Wipo information: entry into national phase |
Ref document number: MX/A/2011/003293 Country of ref document: MX |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2011528421 Country of ref document: JP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2738973 Country of ref document: CA |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2775/DELNP/2011 Country of ref document: IN |
|
ENP | Entry into the national phase |
Ref document number: 2009299656 Country of ref document: AU Date of ref document: 20090930 Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2009759968 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2011112054 Country of ref document: RU |
|
WWE | Wipo information: entry into national phase |
Ref document number: 13121588 Country of ref document: US |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01E Ref document number: PI0919523 Country of ref document: BR Free format text: APRESENTE DOCUMENTOS COMPROBATORIOS QUE EXPLIQUEM A DIVERGENCIA NO NOME DE UM DOS INVENTORES QUE CONSTA NA PUBLICACAO INTERNACIONAL WO2010/038016 DE 08/04/2010 "ANTONY JAMES BODEN" E O CONSTANTE DA PETICAO INICIAL NO 020110030423 DE 30/03/2011 "JAMES ANTONY BODEN". |
|
ENP | Entry into the national phase |
Ref document number: PI0919523 Country of ref document: BR Kind code of ref document: A2 Effective date: 20110330 |