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US20110272069A1 - Wrought magnesium alloy - Google Patents

Wrought magnesium alloy Download PDF

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Publication number
US20110272069A1
US20110272069A1 US12/674,120 US67412008A US2011272069A1 US 20110272069 A1 US20110272069 A1 US 20110272069A1 US 67412008 A US67412008 A US 67412008A US 2011272069 A1 US2011272069 A1 US 2011272069A1
Authority
US
United States
Prior art keywords
alloy
magnesium
casting
lanthanum
temperature
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Abandoned
Application number
US12/674,120
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English (en)
Inventor
Matthew Robert Barnett
Christopher Huw John Davies
Aiden Graeme Beer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Cast CRC Ltd
Original Assignee
Cast CRC Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from AU2007904722A external-priority patent/AU2007904722A0/en
Application filed by Cast CRC Ltd filed Critical Cast CRC Ltd
Assigned to CAST CRC LIMITED reassignment CAST CRC LIMITED ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: DAVIES, CHRISTOPHER HUW JOHN, BARNETT, MATTHEW ROBERT, BEER, AIDEN GRAEME
Publication of US20110272069A1 publication Critical patent/US20110272069A1/en
Priority to US14/613,234 priority Critical patent/US9745647B2/en
Abandoned legal-status Critical Current

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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/005—Continuous extrusion starting from solid state material
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/04—Alloys based on magnesium with zinc or cadmium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon

Definitions

  • the present invention relates to a magnesium alloy, in particular to a wrought magnesium alloy.
  • a wrought alloy is an alloy which has the potential to be worked into a shape or condition after casting.
  • the present invention also relates to a method of manufacturing a wrought magnesium alloy article.
  • a magnesium-based alloy consisting of, by weight:
  • the balance being magnesium except for incidental impurities.
  • a magnesium-based alloy consisting of, by weight:
  • the balance being magnesium except for incidental impurities.
  • the rare earth content is lanthanum, more preferably more than 90%.
  • the rare earth content may be 100% lanthanum, less any incidental impurities.
  • the rare earth content is at least 0.1, more preferably at least 0.2%, preferably no more than 0.4%, preferably no more than 0.3%.
  • the rare earth content may be greater than 0.25%.
  • the rare earth content may be added as a “misch metal” which is understood to comprise an amount of at least two of the rare earth elements.
  • rare earth and “rare earth elements” is understood to mean any of the elements with atomic numbers 57 (lanthanum) through 71 (lutetium),
  • the rare earth content may also comprise cerium.
  • the cerium content is less than the lanthanum content.
  • the rare earth content may also comprise praseodymium and/or neodymium, typically only in small amounts ( ⁇ 5% of the total rare earth content).
  • the lanthanum content of the alloy is 0.05 to 0.5%, more preferably at least 0.09%, more preferably at least 0.1%, more preferably at least 0.15%, preferably no more than 0.4%, more preferably no more than 0.3%.
  • the lanthanum content of the alloy may be greater than 0.25%.
  • the manganese content is greater than 0.6%, more preferably less than 1.3%, more preferably 0.7 to 1.2%, and most preferably about 1%.
  • Zinc is an optional component of the alloy, which may be added to strengthen the alloy.
  • the zinc content is preferably less than 1.3%, more preferably 0.2 to 1.3%, more preferably 0.2 to 1.1%, more preferably 0.4 to 1.1%, and most preferably 0.5 to 1.0%.
  • Incidental impurities may comprise aluminium and silicon.
  • the weight of aluminium in the alloy is preferably no greater than 0.03%.
  • the weight of silicon in the alloy is preferably no greater than 0.03%.
  • Strontium is an optional component of the alloy, which may be added to strengthen the alloy.
  • the strontium content is preferably greater than 0.01%, preferably no more than 0.1%, more preferably about 0.02%.
  • a wrought magnesium alloy article comprising an amount of an alloy according to the first or second aspect of the present invention which has been worked into a shape or condition.
  • a wrought magnesium alloy article comprising the steps of:
  • Step (c) may comprise extruding, forging or any other type of working of the casting.
  • the method may also comprise the step of:
  • step (d) ageing the casting at a second temperature for a second period of time, after step (b) and prior to step (c).
  • the first temperature is 450° C.-650° C., more preferably 540° C.-580° C.
  • the first period of time is 0.5-6 hours, more preferably 1-5 hours.
  • the second temperature is 300° C.-400° C., more preferably 325° C.-375° C.
  • the second period of time is 2-24 hours, more preferably 5-16 hours.
  • a method of manufacturing a wrought magnesium alloy article comprising the steps of:
  • Step (c) may comprise extruding, forging or any other type of working of the casting.
  • the method may also comprise the step of:
  • step (d) ageing the worked casting at a second temperature for a second period of time, after step (b) and prior to step (c).
  • the first temperature is 450° C.-650° C., more preferably 540° C.-580° C.
  • the first period of time is 6-20 hours, more preferably 8-14 hours, most preferably 12 hours.
  • the second temperature is 300° C.-400° C., more preferably 325° C.-375° C.
  • the second period of time is 2-24 hours, preferably 5-16 hours.
  • the magnesium-based alloy may be any magnesium-based alloy which is amenable to precipitation.
  • the magnesium-based alloy may be the alloy according to the first or second aspect of the present invention.
  • the magnesium-based alloy consists of, by weight:
  • the balance being magnesium except for incidental impurities.
  • the rare earth content is 0.1 to 0.5%, more preferably 0.2 to 0.5%, more preferably, 0.3 to 0.5%, most preferably about 0.4%.
  • the rare earth content is provided by a “misch metal”.
  • the rare earth content comprises at least lanthanum.
  • the rare earth content also comprises cerium.
  • a number of alloys according to embodiments of the present invention were cast as 2 kg billets by gravity casting. It is noted however, that other suitable casting methods such as direct chill casting may be employed. Table 1 below sets out the contents of the magnesium alloys prepared.
  • magnesium constituted the balance except for incidental impurities.
  • impurities were found to comprise approximately 0.01 wt % aluminium and less than 0.002 wt % iron in all of the alloys.
  • FIGS. 1A and 1B show the microstructure of alloys A and B as cast. Alloy B, which contains 0.5 wt % zinc has smaller grains than alloy A, which contains no zinc but the same amounts of manganese and lanthanum.
  • Samples of alloys A and B were subsequently extruded after being subjected to a solutionising pre-treatment in which the samples were heated at approximately 580° C. for approximately 1 hour.
  • the samples were extruded at different billet temperatures and ram speeds (ie. the speed at which the alloy is extruded in mm/sec) to establish the extrusion limits of these alloys.
  • Extrusion limits of an alloy are understood to be the limits of the speed and temperature at which the alloy can be satisfactorily extruded. At high billet temperatures, cracking may occur in the extruded alloy if the ram speed is too high.
  • the maximum ram speed at which the alloy may be extruded is limited by the load capacity of the extrusion press, such that at a certain low temperature, the alloy is not extrudable at all.
  • FIGS. 2A and 2B are extrusion limit diagrams of alloys A and B. It is noted that alloy A has wider extrusion limits than alloy B. It would therefore appear that adding the 0.5% zinc (alloy B) narrows the extrusion limits of the alloy. For all alloys A and B, however, FIGS. 2A and 2B demonstrate that they may be satisfactorily extruded at high speeds and high temperatures.
  • FIG. 3 shows the extrusion limit windows for a number of industry common alloys, AZ31, ZK60, AZ61 and ZM21 which have the following nominal compositions:
  • alloys A and B compares favourably with the industry alloys, in particular AZ31, which is the most commonly used.
  • FIG. 4 provides an extrusion limit diagram which compares alloy H to alloy A.
  • FIG. 4 demonstrates that alloy A has improved extrudability over alloy H. Without wishing to be bound by theory it is believed that the improved extrudability of alloy A (over alloy H) is due to the lanthanum addition not lowering the solidus temperature nor increasing the hot working flow stress as much as the misch metal addition consisting predominantly of cerium.
  • Alloy A at least, was found to have a proof stress in tension of approximately 160-200 MPa and a proof stress in compression of 110 MPa, which may be improved by ageing of the alloy. It is noted that the proof stress in tension is dependent on the solutionising temperature and the grain size of the alloy.
  • alloys A and B were also measured following extrusion (the alloys having been subjected to a solutionising treatment prior to extrusion) at a ram speed of 15 mm/sec for different billet temperatures. It was found that a lower grain size was achieved at lower extruding temperatures.
  • Sample Castings of alloys A to F were also extruded at a ram speed of 15 mm/sec and 375° C. following a pre-treatment of the cast billets. Different pre-treatments were carried out and the grain size of the extruded alloys measured. Each pre-treatment first involved a solutionising step in which the casting was heated at a temperature of 500 to 580° C. Some pre-treatments further involved an ageing step in which, after quenching the heated casting, further heating of the casting at a lower temperature (approximately 350° C.). Table 3 below provides details of the pre-treatments carried out, and the resulting grain size of the extruded alloys.
  • alloys A and B that a longer homogenisation time (ie. time spent at the solutionising temperature) appears to result in finer grain sizes being obtained in the extruded alloy. It is also noted that the addition of zinc (alloy B) appears to render the alloy sensitive to aging prior to extrusion, such that finer grain sizes may be obtained by ageing magnesium-manganese-lanthanum alloys also containing zinc.
  • FIG. 5 shows the stability of the microstructure of alloy A against AZ31 after compression at 350° C. at a strain of 1.5, followed by annealing at the same temperature.
  • the grain size of AZ31 increases from 6 microns to 25 microns, while the grain size of alloy A remains generally unchanged during this time.
  • alloy A to maintain a fine grain size is due to the lanthanum addition as the lanthanum restricts the mobility of grain boundaries during recrystalisation.
  • the stability of the grain size of the alloy means that when it is worked (ie. extruded or forged) at elevated temperatures, a small grain size is maintained during slow cooling and/or subsequent annealing.
  • alloy A and AZ31 were both extruded under the same conditions (billet temperature of 370° C., extrusion speed of 6 m/min)
  • the average grain size developed in AZ31 was three times greater than that of alloy A (23 microns compared to 7 microns). This can also be seen in the microstructures shown in the comparative micrographs of FIG. 6 . In general, however, it is shown that advantageously, lanthanum reduces the grain size of the alloy.
  • FIG. 7 shows the change in resistivity for the increase in heat treatment times at the various temperatures. It can be seen from FIG. 7 that the resistivity remains fairly constant at intermediate temperatures, but increases at 580° C. possibly due to the dissolving of precipitates and decreases at 460° C. possibly due to precipitation and/or to the coarsening of precipitates already present in the alloy from casting.
  • solution treatment at 580° C. did yield a slightly smaller grain size relative to the untreated billet (when the heating time was 1 hour).
  • solution treatment at 460° C. resulted in larger extruding grain sizes. Without wishing to be bound by theory, it is believed that this is due to particle precipitation occurring at 460° C. leaving less lanthanum in solid solution to inhibit grain coarsening.
  • solution treatment at 580° C. enhanced the tensile ductility of the untreated alloy whereas treatment at 460° C. had little or no effect on the ductility.
  • Alloys were also prepared to determine the effect of the addition of strontium to the alloy. Alloys were prepared containing (by weight) 1.0% manganese, 0.2% lanthanum and either 0.02% or 0.04% strontium with the balance magnesium except for incidental impurities. These alloys were extruded at 375° C. and 15 mm/s and the grain size and mechanical properties of the extruded alloys were measured. Table 6 below sets out these properties as compared to Alloy A (having 1.0% manganese, 0.2% lanthanum, 0% strontium, balance magnesium).
  • aluminium and silicon were found to have a deleterious effect on the grain size and ductility of the alloy. Without wishing to be bound by theory, it is understood that the deleterious effect caused by aluminium and silicon is due to both aluminium and silicon readily forming Mg—Al—La and Mn—Si—La particles respectively, which are at least partially responsible for the increase in grain size because some of the lanthanum content is used up in these particles.
  • an additional benefit of a strontium addition to the alloy is that is suppresses the detrimental effect of aluminium.
  • an alloy containing (by weight) 1.0% manganese, 0.2% lanthanum, 0.5% aluminium, 0.04% strontium, with the balance magnesium except for incidental impurities was prepared and extruded at 375° C. and 15 mm/s. This alloy was found to have a grain size of 7.4 ⁇ m, a uniform elongation of 12.1% and a total elongation of 19.6%. This compares favourably to the alloy containing 0.5% aluminium and 0% strontium, the properties for which are set out in Table 8 above.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Extrusion Of Metal (AREA)
  • Forging (AREA)
US12/674,120 2007-08-31 2008-08-29 Wrought magnesium alloy Abandoned US20110272069A1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US14/613,234 US9745647B2 (en) 2007-08-31 2015-02-03 Wrought magnesium alloy

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
AU20077904722 2007-08-31
AU2007904722A AU2007904722A0 (en) 2007-08-31 Wrought magnesium alloy
PCT/AU2008/001285 WO2009026652A1 (en) 2007-08-31 2008-08-29 Wrought magnesium alloy

Related Parent Applications (1)

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PCT/AU2008/001285 A-371-Of-International WO2009026652A1 (en) 2007-08-31 2008-08-29 Wrought magnesium alloy

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US14/613,234 Continuation US9745647B2 (en) 2007-08-31 2015-02-03 Wrought magnesium alloy

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US14/613,234 Expired - Fee Related US9745647B2 (en) 2007-08-31 2015-02-03 Wrought magnesium alloy

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US (2) US20110272069A1 (zh)
EP (1) EP2183399B1 (zh)
JP (1) JP5525444B2 (zh)
CN (2) CN104694804A (zh)
WO (1) WO2009026652A1 (zh)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180087133A1 (en) * 2015-04-08 2018-03-29 Baoshan Iron & Steel Co., Ltd. Formable magnesium based wrought alloys

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009025511A1 (de) * 2009-06-19 2010-12-23 Qualimed Innovative Medizin-Produkte Gmbh Implantat mit einem vom Körper resorbierbaren metallischen Werkstoff
JP5421694B2 (ja) * 2009-08-24 2014-02-19 テクマグ・アクチエンゲゼルシャフト マグネシウム合金
CN105525172A (zh) 2014-11-13 2016-04-27 比亚迪股份有限公司 一种镁合金及其制备方法和应用
CN108677073A (zh) * 2018-09-03 2018-10-19 重庆大学 一种高强度变形镁合金及其制备方法
CN113293329A (zh) * 2020-02-21 2021-08-24 宝山钢铁股份有限公司 一种低成本高强度高导热镁合金材料及其制造方法

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US2221254A (en) * 1939-11-13 1940-11-12 Dow Chemical Co Magnesium base alloy
US2270190A (en) * 1940-06-15 1942-01-13 Dow Chemical Co Magnesium base alloy
GB858200A (en) * 1958-07-24 1961-01-11 Magnesium Elektron Ltd Improvements in or relating to magnesium base alloys containing manganese
US3157496A (en) * 1962-09-13 1964-11-17 Dow Chemical Co Magnesium base alloy containing small amounts of rare earth metal
GB1463609A (en) * 1974-12-30 1977-02-02 Magnesium Elektron Ltd Magnesium alloys
JP3509163B2 (ja) * 1993-02-12 2004-03-22 マツダ株式会社 マグネシウム合金製部材の製造方法
DE19915276A1 (de) * 1999-04-03 2000-10-05 Volkswagen Ag Verfahren zum Herstellen einer Magnesiumlegierung durch Strangpressen und Verwendung der stranggepreßten Halbzeuge und Bauteile
AUPS311202A0 (en) * 2002-06-21 2002-07-18 Cast Centre Pty Ltd Creep resistant magnesium alloy
JP4433916B2 (ja) * 2004-07-13 2010-03-17 株式会社豊田中央研究所 塑性加工用マグネシウム合金およびマグネシウム合金部材

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180087133A1 (en) * 2015-04-08 2018-03-29 Baoshan Iron & Steel Co., Ltd. Formable magnesium based wrought alloys

Also Published As

Publication number Publication date
EP2183399A1 (en) 2010-05-12
JP2010537052A (ja) 2010-12-02
US9745647B2 (en) 2017-08-29
CN101815801A (zh) 2010-08-25
EP2183399A4 (en) 2011-09-07
CN104694804A (zh) 2015-06-10
WO2009026652A1 (en) 2009-03-05
US20150218680A1 (en) 2015-08-06
EP2183399B1 (en) 2013-04-10
JP5525444B2 (ja) 2014-06-18

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Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:BARNETT, MATTHEW ROBERT;DAVIES, CHRISTOPHER HUW JOHN;BEER, AIDEN GRAEME;SIGNING DATES FROM 20110208 TO 20110209;REEL/FRAME:026006/0658

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