CN1938441A - High-strength-toughness magnesium alloy and its preparing method - Google Patents
High-strength-toughness magnesium alloy and its preparing method Download PDFInfo
- Publication number
- CN1938441A CN1938441A CNA2005800098757A CN200580009875A CN1938441A CN 1938441 A CN1938441 A CN 1938441A CN A2005800098757 A CNA2005800098757 A CN A2005800098757A CN 200580009875 A CN200580009875 A CN 200580009875A CN 1938441 A CN1938441 A CN 1938441A
- Authority
- CN
- China
- Prior art keywords
- alloy
- casting
- magnesium
- crucible
- 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.)
- Granted
Links
- 229910000861 Mg alloy Inorganic materials 0.000 title claims abstract description 41
- 238000000034 method Methods 0.000 title claims abstract description 19
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 143
- 239000000956 alloy Substances 0.000 claims abstract description 143
- 238000010438 heat treatment Methods 0.000 claims abstract description 66
- 238000005266 casting Methods 0.000 claims abstract description 42
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 25
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 25
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 19
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 19
- 239000011777 magnesium Substances 0.000 claims abstract description 19
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 17
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims abstract description 16
- 239000011572 manganese Substances 0.000 claims abstract description 14
- 230000032683 aging Effects 0.000 claims abstract description 13
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 12
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 239000010703 silicon Substances 0.000 claims abstract description 8
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 6
- 239000011575 calcium Substances 0.000 claims abstract description 6
- 229910052751 metal Inorganic materials 0.000 claims abstract description 3
- 239000002184 metal Substances 0.000 claims abstract description 3
- 239000004411 aluminium Substances 0.000 claims description 23
- 238000011282 treatment Methods 0.000 claims description 18
- 229910001122 Mischmetal Inorganic materials 0.000 claims description 13
- 229910052684 Cerium Inorganic materials 0.000 claims description 12
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 claims description 12
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 10
- 239000010931 gold Substances 0.000 claims description 10
- 229910052737 gold Inorganic materials 0.000 claims description 10
- 238000002360 preparation method Methods 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 8
- 238000007906 compression Methods 0.000 claims description 7
- 230000006835 compression Effects 0.000 claims description 7
- 239000000155 melt Substances 0.000 claims description 5
- 238000012545 processing Methods 0.000 claims description 5
- 238000005275 alloying Methods 0.000 claims description 4
- 238000000465 moulding Methods 0.000 claims description 4
- 238000007528 sand casting Methods 0.000 claims description 4
- 239000002893 slag Substances 0.000 claims description 4
- 238000006073 displacement reaction Methods 0.000 claims description 3
- 238000010792 warming Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 2
- 230000008018 melting Effects 0.000 claims description 2
- 239000000843 powder Substances 0.000 claims 1
- 239000011701 zinc Substances 0.000 abstract description 24
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 abstract description 10
- 229910052725 zinc Inorganic materials 0.000 abstract description 10
- 238000001125 extrusion Methods 0.000 abstract description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 150000002739 metals Chemical class 0.000 abstract 1
- 239000004576 sand Substances 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 15
- 238000003723 Smelting Methods 0.000 description 14
- 239000002245 particle Substances 0.000 description 12
- 239000013078 crystal Substances 0.000 description 11
- 238000012360 testing method Methods 0.000 description 11
- 239000007789 gas Substances 0.000 description 10
- 238000004455 differential thermal analysis Methods 0.000 description 9
- 229910052761 rare earth metal Inorganic materials 0.000 description 9
- 150000002910 rare earth metals Chemical class 0.000 description 8
- 239000000243 solution Substances 0.000 description 8
- -1 aluminium zinc-manganese Chemical compound 0.000 description 7
- 239000000126 substance Substances 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 6
- FAWGZAFXDJGWBB-UHFFFAOYSA-N antimony(3+) Chemical compound [Sb+3] FAWGZAFXDJGWBB-UHFFFAOYSA-N 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910010271 silicon carbide Inorganic materials 0.000 description 4
- 239000011573 trace mineral Substances 0.000 description 4
- 235000013619 trace mineral Nutrition 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 2
- 229910018573 Al—Zn Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910052790 beryllium Inorganic materials 0.000 description 2
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 2
- 229910052797 bismuth Inorganic materials 0.000 description 2
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 2
- 239000003086 colorant Substances 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 238000007788 roughening Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910052712 strontium Inorganic materials 0.000 description 2
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 description 2
- 229910002058 ternary alloy Inorganic materials 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910021323 Mg17Al12 Inorganic materials 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- 241001201614 Prays Species 0.000 description 1
- 241001417490 Sillaginidae Species 0.000 description 1
- PGTXKIZLOWULDJ-UHFFFAOYSA-N [Mg].[Zn] Chemical compound [Mg].[Zn] PGTXKIZLOWULDJ-UHFFFAOYSA-N 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 239000005030 aluminium foil Substances 0.000 description 1
- 230000003698 anagen phase Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 238000000295 emission spectrum Methods 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 238000002389 environmental scanning electron microscopy Methods 0.000 description 1
- 239000003063 flame retardant Substances 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 238000009616 inductively coupled plasma Methods 0.000 description 1
- 238000002354 inductively-coupled plasma atomic emission spectroscopy Methods 0.000 description 1
- 230000016507 interphase Effects 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 208000020442 loss of weight Diseases 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000000048 melt cooling Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical compound [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 238000010120 permanent mold casting Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000007086 side reaction Methods 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000004611 spectroscopical analysis Methods 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
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
- C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
-
- 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
- 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
Landscapes
- 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)
- Manufacture And Refinement Of Metals (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
The present invention relates to a high-strength, high-toughness cast magnesium alloy and the method thereof, in which the alloy consists substantially of aluminum 3-9 wt%, zinc 3.5-9 wt%, manganese 0.15-1.0 wt%, antimony 0.01-2wt%, and the balance magnesium. The alloy may further comprises an element selected from the group consisting of cerium-riched misch metals, calcium or silicon in 0-2 wt%. In the invention, after the T6 (solution + aging) heat treatment, the mechanical property of the typical alloy of the invention can reach the following requirement: the tensile strength sigma b >=270 Mpa, the yield strength sigma0.2>=140 Mpa, the elongation delta5>=6 %, the Brinell hardness >=70, the ballistic work alpha k >=12J. Some alloys of the invention not only have excellent room temperature mechanical property, but also have good elevated mechanical property. The production cost of the invention is relatively low, and it is suitable to produce in large scale. The alloy of the invention is applicable of the casting process, such as permanent mould casting, sand mould casting, press casting, extrusion casting, and the like.
Description
A kind of high-strength-toughness magnesium alloy and preparation method thereof technical field
The present invention relates to one kind casting ^^ gold and its technology of preparing.The purpose of the present invention is to prepare a kind of low cost, high-intensity high-tenacity cast magnesium alloy by using the means such as alloying and heat treatment.The present invention is applicable not only to the permanent die cast of metal mold, and From is applied to the techniques such as sand casting, compression casting, extrusion casint.Background technology
As a kind of light metal material, magnesium alloy has many advantages, such as high specific strength, fabulous machining and casting character, good damping characteristic, dimensional stability and electromagnetic shielding capability etc..Because with above characteristic, magnesium alloy component has been widely used in many industrial departments, including automobile system, 3C Product（Computer, communication, consumer electronics）Manufacturing industry, military project department etc..In recent years, due to increasingly urgent automobile loss of weight demand, the low-density of magnesium alloy causes it handing over defeated field to generate extremely strong attraction again.The demand of mirror alloy occurs in that a rapid growth phase.
However, for relative aluminium alloy, weaker intensity and/or plasticity seriously limit the application of magnesium alloy（For example, application in terms of light-duty vehicle wheel hub etc., while needing high intensity, high tenacity）.Table 1 gives the tensile mechanical properties of some typical commercial cast magnesium alloys.The tensile mechanical properties composition of typical cast magnesium alloy（Percentage by weight）
^ tensile properties
The other σ of A1 Zn Mn Zrb(MPa)
δ 5(%)
C die casting）
AM60 6.0 - 0.3 - - 220 115 8
AZ91 9.0 0.7 0.3 - - 230 150 3
(casting:）
The 2.6RE of ZE63-5.8-0.7 300 190 10 are from table 1 it follows that the maximum pressure of application amount casts ^ AZ91 alloys at present, and with higher intensity, but X cuns of relatively low plasticity of phase limit its application.In addition, although the alloys of Α Μ 60 have higher plasticity, but less high intensity also limit their extensive application.There is high intensity and high tenacity, such as Ζ Ε 63 simultaneously in spite of a small amount of rare earth alloy of magnesium one, but too high cost and the Technology for Heating Processing of complexity cause these alloys to be difficult to large-area applications.It is slow due to improving
The intensity and plasticity of alloy are the further key points for expanding magnesium alloy application, therefore, and it is very urgent task to develop a kind of low cost, high-strength-toughness magnesium alloy.
Although existing many trials for improving mirror alloy tensile mechanical property, in terms of most of work therein concentrates on the drawing by high temperature mechanical property for improving magnesium alloy, and the raising of these alloy at normal temperature mechanical properties is limited.For example, a kind of magnesium alloy with excellent high temperature performance and compression casting performance of European patent 0879898A1 public affairs Jian, but the alloy disclosed in the invention but has relatively low room temperature strength（Tensile strength<230 MPa) and plasticity（Elongation percentage< 5%) .United States Patent (USP) 20030084968A1 discloses a kind of high-strength creep resistant magnesium alloy, but the alloy disclosed in the invention is also with relatively low temperature-room type plasticity（Elongation percentage< 5%) .United States Patent (USP) 6139651 discloses a kind of continuous alloy of high temperature application, but the room temperature strength and plasticity of the alloy disclosed in the invention are undesirable.Some promising high-strength-toughness magnesium alloys, such as United States Patent (USP) 20010055539A1 are obtained in spite of a few patents, the development of more preferable room temperature high-strength-toughness magnesium alloy also needs to further spread out.
In recent years, although micro-（Rare earth element, beryllium, bismuth, strontium, antimony element etc.）Effect in ^^ gold has carried out more research, but most of work is concentrated on the modification of business ^^ gold and the creep-resistant property for improving alloy.For example, Chinese patent CN1401804 discloses a kind of heat resistanceheat resistant magnesium alloy, conjunction ^^ have 2-10 wt% (percentage by weight, similarly hereinafter）Aluminium, 0.2-2 wt% zinc, 0.1-0.6 wt% manganese, 0.1-2 wt% bismuth, 0.1-1.5 wt% antimony, it is other be magnesium.European patent 1241276 discloses a kind of creep resistant alloy, and the conjunction has the wt% of 1.5- 4.0 aluminium, 0.5-1.8 wt % silicon, 0.05-0.6 wt % rare earth, 0.005-1.5 wty.Strontium or antimony, magnesium is balance.Chinese patent CN1341767 discloses a kind of automobile-used heat resistanceheat resistant magnesium alloy of multicomponent and its casting technique, the alloy contains 5-7 wt% aluminium, 0.5-1.0 wt% zinc, 0.6-1.5 wt% silicon, 0.4-0.7 wt% antimony, 0.1-0.3 wt% rare earth, 0.002 wt% beryllium, magnesium is balance.
On the basis of lot of documents analysis, it was noted that can compression casting area in medium aluminium content, the zinc ternary of one aluminium of magnesium one of medium Zn content, if using the appropriate trace element property, suitably it is heat-treated again, it is understood that there may be develop low cost, the potentiality of high-strength-toughness magnesium alloy.As a result, it has been found that some have the magnesium alloys of these characteristics, the following will discuss.The content of the invention
It is a primary object of the present invention to by reasonable selection alloy element and the suitable heat treatment of use, there is provided a kind of cast magnesium alloy for having high intensity and high tenacity concurrently.
The second object of the present invention is that Elderly gold prepared by the method is applicable not only to permanent die cast, and suitable for techniques such as sand casting, compression casting, extrusion casints.
The third object of the present invention is that magnesium alloy prepared by the method not only has excellent room-temperature mechanical property, and some alloys can also have outstanding mechanical behavior under high temperature.
The fourth object of the present invention is the magnesium alloy of method preparation in addition to These characteristics, and the production cost of alloy is relatively low.
The most important discovery of the present invention is：Medium aluminium content and medium Zn content constitute high-strength-toughness magnesium alloy foundational system；The addition and suitable Technology for Heating Processing of trace element further make alloy reach optimal mechanical property.
By weight percentage, the aluminium content in alloy of the present invention is 3 ~ 9 wt%;Zn content is 3.5 ~ 9 wt%;Manganese content is 0.15-1.0 wt%;Antimony content is 0.01 ~ 2 wt%;Content of magnesium is balance；Cerium-rich mischmetal that can also be further containing 02 wt% in alloy, calcium, certain element of silicon thrin.
The activeness and quietness mechanism of the present invention is as follows：1), the solution strengthening mechanism of element.2) it is, secondary to fold phase strengthening mechanism：With the increase of Zn content, Mg17Al12Mutually gradually decrease, while Mg-Al- Ζ η Ξ members phase and magnesium zinc Binary-phase gradually increase；In addition, add after the trace element such as Mn, Sb, according to new particulates reinforcements or particle such as Al-Mn, M^Sba etc. can be produced.3), the addition of some elements（Such as antimony）Can also crystal grain thinning and the continuous fragility secondary-precipitated phase that is distributed on crystal boundary, so as to play a part of improving intensity, plasticity and the casting character of alloy.4) Technology for Heating Processing, can further lift the mechanical property of alloy by adjusting the number and shape of secondary-precipitated phase.
Aluminium（A1) ： 3〜9 wt%
Aluminium element not only for improve gold room temperature strength and hardness for be very effective, and by widen alloy freezing range so that ^^ gold be easier to casting.In order to which the aluminium content obtained in obvious reinforcing effect, alloy should at least 3wt%;But, too high aluminium content can have a negative impact to the plasticity of alloy.Therefore, the maximum of the aluminium content of alloy is set to 9 t% in the present invention.
Zinc（Zn) ： 3.5〜9 wt%
In the magnesium alloy, Zn-ef ficiency is another important alloying element in addition to aluminum.Zinc and aluminium are used for improving the room temperature strength and casting character of alloy jointly in the present invention.It is well known, however, that in Mg-Al-Zn Alloy system, if the matching of zinc and aluminium is improper, it will the hot cracking tendency of increase alloy, deteriorating casting forming function.The present invention is according to the die casting performance of the zinc ternary alloy system of one aluminium of magnesium one and the relation of aluminium Zn content（Referring to accompanying drawing 1), by selecting suitable aluminium, Zn content, and in some trace elements（Such as antimony）In the presence of, so as to obtain the magnesium alloy of relatively low hot cracking tendency on the basis of alloy die cast performance is ensured.Therefore, the Zn content in alloy of the present invention at least should be 3.5 wt%.Further, since low-alloyed plasticity can drop in too high Zn content, 9 wt% are not to be exceeded in highest Zn content.
Manganese (Mn)： 0.15-1 wt%
Manganese element is added in the form of the manganese intermediate alloy of aluminium one in alloy of the present invention.Although effect of the manganese in terms of strength of alloy is improved be not obvious, it can mutually be played a part of some by the manganese particle of aluminium one being present in primary crystal crystal grain and improve yield strength.The main function of manganese in the present invention is the decay resistance for improving alloy.Manganese can be with the impurity element in alloy during alloy melting（Such as iron, nickel）Compound is formed, crucible bottom is deposited to, goes the removal of impurity, eliminate illeffects of these elements to alloy decay resistance.The addition of manganese is limited by its low solid solubility, and the addition of manganese is 0.15-1 wt% in the present invention.
Antimony（Sb) ； 0.01-2 wt%
The powder-form that antimony element in the present invention is either wrapped up with aluminium-foil paper is added, or is added with bulk form.A small amount of antimony element can refine primary crystal crystal grain and secondary-precipitated phase, so as to play a part of improving alloy mechanical property and mitigate hot cracking tendency.But, when antimony content surpasses 2 wt%, the Mg3Sb of roughening2Particle can reduce mechanical property on the contrary.Therefore, antimony content should be controlled in 0.01% ~ 2wt% in the present invention.
Other elements： 0-2 wt%
0 ~ 2 wt% cerium-rich mischmetal, calcium, certain element of silicon thrin can also further be contained in alloy in the present invention.
Cerium-rich mischmetal in the present invention is commercially available prod, and its manufacturer is Baotou HUAMEI RE products Co., Ltd..50% or so is cerium in cerium-rich mischmetal, and other main components are lanthanum and neodymium.A small amount of rare earth, which is added, can improve the hardness and mechanical behavior under high temperature of magnesium alloy, but on the one hand excessive rare earth can increase cost, on the other hand can produce the particle precipitated phase of roughening and cause the decline of mechanical property and casting character.Content of rare earth should be controlled in 0 ~ 2 wt%, it may be more desirable to be limited in 0 ~ 1 wt%.
The addition of calcium constituent can not only play fire-retardant effect, and can improve the mechanical behavior under high temperature and creep resistance of alloy.However, the addition of calcium can reduce casting character and aggravate the hot cracking tendency of alloy.
The addition of element silicon can also improve the mechanical behavior under high temperature and creep resistance of alloy, but excessive element silicon can produce thick M S Willing and produce and cause the decline of mechanical property.
The smelting of alloy and casting technique can be divided into the following steps in the present invention：
1) first setting crucible target temperature, (TC is begun to warm up as 700 ~ 75；Then various dispensings are put and be preheated in an oven
140 ~ 200 °C, while the coverture that the ^% of purpose alloy gross weight 0.6 will be accounted for（The coverture that can be commonly used using magnesium alloy）It is put into for being toasted in case；In addition, rich casting is preheated into 20040 (TC in the batch-type furnace that another sunset is foretold with mould.
2) when crucible is warming up to 280 ~ 320 °C, it is passed through C02Gas displacement is carried out in gas to crucible, then adds Λ 30% ~ 50% coverture toasted in crucible bottom, then preheated pure magnesium dispensing is put into crucible afterwards.
3) pure magnesium dispensing melts and waits crucible temperature stable after 700 750 °C, sequentially adds the various dispensings of preheating from high to low according to fusing point, then melt is stirred in about 8 ~ 10；During this, the remaining coverture toasted is added as one sees fit, is defined so that surface is non-ignitable.
4) crucible temperature is stable after 700 750 °C, and melt stands 4 ~ 6 minutes, by percent by volume, in 99 ~ 99.5% air（Or C02) + 0.5~1% SF6Surface scum is drawn out under mixed gas protected；
5) draw after slag finishes, maintain crucible temperature 700 ~ 750.C, by percent by volume, in 99 ~ 99.5% air（Or C02) + 0.5-1% SF6Mixed gas protected lower cast molding.
The heat treatment of the present invention largely have impact on the mechanical property of alloy.The alloy heat treatment mode of the present invention can be divided into T4 (solution treatment）, T5 (Ageing Treatments）, T6 (after solution treatment again plus Ageing Treatment）Three kinds, introduce separately below.,
T4 solution treatment is preferably in protective atmosphere（Such as argon gas, 99 ~ 99.5% air（Or C02) + 0.5-1% SF6Mixed gas etc.）Middle to carry out, its temperature range is that 340 0 (TC is simultaneously closely related with Zn content.It is, in general, that the solid solubility temperature of magnesium alloy should be lower than the solidus temperature of alloy 10 ~ 20 °C.The solidus temperature of the zinc ternary alloy system of one aluminium of magnesium one refers to accompanying drawing 2.In addition, some elements（Such as antimony）Addition can produce minimal effect to solidus temperature, therefore, more accurate solidus temperature can be determined by the differential thermal analysis data of alloy.It can be taken as 8 ~ 24 hours as the time of T4 solution treatment.
The temperature of T5 Ageing Treatments is taken as 70 ~ 200 °C, and the time of Ageing Treatment can be taken as 8 ~ 24 hours.As for T6 heat treatments, it can be understood as a kind of combination of T4 and T5 heat treatments.Specifically, it is first progress T4 heat treatments, T5 heat treatments is then carried out again.
Because heat treatment changes the distribution mode and quantity of particulates reinforcements, therefore it significantly affects mechanical property.It is, in general, that the sample of T4 solution treatment is dissolved in matrix again due to interphase, so plasticity and shock resistance can be improved, but yield strength can decrease.T5 Ageing Treatments can eliminate residual stress and improve mechanical property to a certain extent.T6 processing is due to that can redistribute the number and shape of secondary-precipitated phase, so the intensity and hardness of alloy can be obviously improved, but the plasticity of alloy can decline.
The exemplary alloy of the present invention is in T6 (solid solutions+timeliness）After heat treatment, its room-temperature mechanical property can reach：Tensile strength cjb270MPa, yield strength.^ ^.^^, extension56%, Brinell hardness 70, ballistic work otk 12J。
The invention has the advantages that：
1) magnesium alloy for preparing of the present invention, has the characteristic of high-intensity high-tenacity concurrently, is particularly suitable for lightweight, high-strength, high-ductility uses material demand, such as automotive hub.
2) magnesium alloy prepared by the present invention, not only with excellent room-temperature mechanical property, some alloys also have preferable mechanical behavior under high temperature.
3) cost performance of the present invention is high.Raw materials are easy to get, and cost is low, suitable for large-scale production.
4) present invention smelts and casting technique simple and stable.The alloy element that the present invention is used, does not occur obvious side reaction, process stabilizing with Iron reutilization wall or coverture.
5) applicable craft scope of the present invention is wide.The present invention is applicable not only to permanent mold casting, is equally applicable to the techniques such as sand casting, compression casting, extrusion casint.Brief description of the drawings
Scheme the compression casting performance and embodiment alloy position schematic diagram of l Vlg-Al-Zn ≡ member alloys.
Fig. 2 is Mg-Al-ZnH member alloy phase diagrams（Solid phase surface）And embodiment alloy position schematic diagram.
Fig. 3 is the DTA curve of the alloy of the embodiment of the present invention 1., Fig. 4 is the as-cast structure of the alloy of the embodiment of the present invention 1.
Fig. 5 is Mg3Sb2The distribution schematic diagram in the alloy of embodiment 1 after T4 heat treatments, at arrow mark is Mg3Sb in figure2Distribution of the particle in the alloy of embodiment 1.
Fig. 6 is tissue of the alloy of embodiment 1 after T4 heat treatments.
Fig. 7 is tissue of the alloy of embodiment 1 after the heat treatments of Τ 6.
Fig. 8 is the room-temperature mechanical property contrast situation of three kinds of alloys (embodiments 1 of Α Μ 60, Α Ζ 9) as cast condition.
Fig. 9 is three kinds of alloys（Α Μ 60, Α Ζ 91, embodiment 1) Τ 6 heat treatment state room-temperature mechanical property contrast situation.Figure 10 is four kinds of alloys（Embodiment 1, embodiment 2, embodiment 3, AZ91) Τ 6 heat treatment state room-temperature mechanical property contrast situation.
Figure 11 is four kinds of alloys（Embodiment 1, embodiment 2, embodiment 3, AZ91) Τ 6 heat treatment state 150 mechanicals behavior under high temperature contrast situation.
Figure 12 is three kinds of alloys（Embodiment 4, embodiment 5, AZ91) Τ 6 heat treatment state 150 mechanicals behavior under high temperature contrast situation.Embodiment
The high-strength-toughness magnesium alloy of the present invention is described in detail with reference to embodiment：
Embodiment 1
I), alloy is constituted
Three kinds of magnesium alloys are prepared from using commercial high-purity raw material in low-carbon steel crucible.In three kinds of alloys, the commercial trade mark
It is comparative example alloy that ^ AM60 are closed in AZ91 and experiment.The chemical composition of three kinds of magnesium alloys is analyzed using the atomic emission spectrum of inductively coupled plasma one (ICP-AES) technology.The chemical composition of three kinds of ^ ^ gold is shown in 2.
2. the chemistry of three kinds of alloys is into ^ (percentage by weight wt %) mouth ^ aluminium zinc-manganese w magnesium
9.00 1.03 0.29-balances of AZ91
AM60 5.92-0.28-balance
The balance of embodiment 1 5.88 3.89 0.30 0.51
II), alloy smelting and casting
The smelting of alloy in the crucible and resistance furnace of 15 kg capacities ' carry out.Crucible and casting molds use low-carbon steel material.Below by taking embodiment 1 as an example, smelting and the casting technique of alloy are elaborated.
1) crucible target temperature is set as 720 °C, is begun to warm up；Then the various dispensings such as pure magnesium, fine aluminium, aluminium manganese intermediate alloy, star antimony, pure zinc are put and is preheated to 160 °C in an oven, purpose alloy gross weight 2wt % RJ-2 covertures (RJ-2 covertures manufacturer is Sichuan Lan De high-techs Industries, Ltd, its product designation ZS-MF1) will be accounted for simultaneously to be put into baking oven and toast；Casting in other batch-type furnace is preheated to 30CTC with mould.
2) when crucible is warming up to 300 °C, it is passed through C02Gas displacement is carried out in gas to crucible, 1/2 or so the coverture toasted is then added in crucible bottom, then preheated pure magnesium dispensing is put into crucible afterwards.
3) pure magnesium dispensing melts and waits crucible temperature stable after 720 °C, sequentially adds the various dispensings of preheating from high to low according to fusing point（Fine aluminium, aluminium manganese intermediate alloy, star antimony, pure zinc etc.）, then melt be stirred about 8 ~ 10 minutes；During this, the remaining coverture toasted is added as one sees fit, is defined so that surface is non-ignitable.
4) crucible temperature is stable after 72CTC, and melt stands 4^ minutes, by percent by volume, in 99 ~ 99.5% air（Or C02) + 0.5~1% SF6Slag is drawn under mixed gas protected；
5) draw after slag finishes, maintain crucible temperature stable at 720 °C, by percent by volume, in 99 ~ 99.5% air（Or C02) + 0.5-1% SF6Mixed gas protected lower cast molding.
The smelting of AZ91 and AM60 alloys and casting technique are similar with AZY641, and simply the addition of various alloying elements is different.
Π Ι), the heat treatment of alloy：
The heat treatment of three kinds of alloys can be divided into T4 (solid solutions）, T5 (timeliness）, T6 (solid solutions+timeliness）Three kinds：
A) T4 is heat-treated：T4 heat treatment temperatures can be deduced from differential thermal analysis (DTA) data of alloy and drawn.For example (refer to Fig. 3), the DTA curve of the alloy of embodiment 1 shows there are two flex points in the place close to solidus（377 °C,
354°C).According to experiment, the T4 heat treatments of the alloy of embodiment 1 can not surpass il370 °C.The T4 heat treatment temperatures of the alloy of embodiment 1 are 370 °C, and the time is 12 hours.The T4 heat treatment temperatures of AZ91 and AM60 alloys are 410 °C, and heat treatment time was controlled at 16 ~ 24 hours.The sample that T4 heat treatments are finished, which is used, is air-cooled to room temperature.
B) T5 is heat-treated：Three kinds of alloys can be using identical T5 heat treatments.The temperature control of T5 heat treatments is at 180 °C, and the temperature of T5 heat treatments is 16 hours, and the sample that heat treatment is finished uses and is air-cooled to room temperature.
C) T6 is heat-treated：T6 heat treatments can regard the combination of T4 and T5 heat treatments as.Successively logical respective suitable T4 and the T5 heat treatment stated of every kind of alloy.
IV), Hear tissue characterizations,
Its preparation process of the sample of structure observation is as follows：Using No. 1000 carborundum silicon carbide paper flattened surfaces；Then oil base diamond paste machine light leak is used；Sample surfaces after polishing carry out rotten quarter using the nital of 2% concentration.Surface structure observations are carried out on the electronic scanner microscope Philips XL30 ESEM-FEG/EDAX equipped with spectroscopy device.
Compared to the alloy for not adding antimony element, its primary crystal crystal grain of the as-cast structure of the alloy of embodiment 1 and secondary-precipitated phase have obtained a certain degree of refinement（With reference to Fig. 4).The mechanism of this process is understood that：A small amount of antimony element can generate fusing point up to 1228 °C of M S particles with magnesium；TheseThe particles of ^ 81 can preferentially be generated in melt cooling process, and the heterogeneous nucleating center that some particles therein will turn into primary phase plays a part of refining primary phase；Other Mg3Sb2Particle appears in the liquid phase forward position constantly grown causes the secondary precipitation distributed mutually of more disperse so as to which reciprocation occurs for the precipitation with secondary phase.In ESEM and power spectrum observation, Mg3Sb2Particle is present not only in primary crystal intra-die, and also appears on crystal boundary and (refer to Fig. 5).
Fig. 6 and Fig. 7 give the Microstructure evolution of the alloy of embodiment 1 caused by different heat treatment modes.From fig. 6 it can be seen that T4 heat treatments cause most secondary-precipitated phase to dissolve in again in primary phase, the particle remained in figure is with dystectic particle（Such as MfeSbz and Al-Mn^）.T6, which is heat-treated, causes solute element to be separated out again from primary grain, and with the formal distribution of more disperse in crystal boundary and intra-die（With reference to Fig. 7).
V), Mechanics Performance Testing
It is prepared by the room temperature mechanical stretch performance samples Reference Chinese national standard GB 6397-86 of alloy.The parallel carpenters square cun of sample is the X 3 (mm) of 30 X 6.The surface of sample is using No. 1000 carborundum paper polishings.The strain rate of tension test is the θ of 1.11 X 1.
The parallel carpenters square cun of high temperature (150 °C) mechanical stretch performance sample of alloy is the X3 of 27X 5 (mm).The surface of sample is using No. 1000 carborundum paper polishings.The strain rate of tension test is 5.55X 104S4。
The Brinell hardness sample preparation of alloy and experimental method refer to GB231-84, and specimen size is 15x15x5 (mm)0It is prepared by the impact property samples Reference Chinese national standard GB T 229-1994 of alloy.The parallel carpenters square cun of sample is 10x10x55
(mm), sample is non-notch sample.
Fig. 8 gives the room-temperature mechanical property contrast of cast alloy (AZ91-F, AM60-F, embodiment 1-F).Fig. 9 gives the room-temperature mechanical property contrast of T6 heat treatment states alloy (AZ91-T6, AM60-T6. embodiment 1-T6).The room temperature mechanical property Chong yield strength tensile strength elongation percentage ballistic work heat treatment state Brinell hardness of the alloy of embodiment 1
(MPa) 10 60 19 of (MPa) (%) (J) as cast condition 216 106
T4 heat treatments 250 101 12 59 30
T5 heat treatments 230 128 7 65 12
T6 heat treatments 285 137 8.5 68 18 are from table 3 it is observed that T4 heat treatments improve the plasticity of the alloy of embodiment 1；T5 heat treatments also improve mechanical property to a certain extent.T6 has been thermally treated resulting in highest yield strength and tensile strength, but sacrifices some plasticity with T4 heat treatment ratios.
Embodiment 1 is shown in Figure 10 with AZ91 Alloy At Room Temperatures mechanical property contrast situation, and the contrast situation of embodiment 1 and the mechanical behavior under high temperature of AZ91 alloys is shown in Figure 11.It can be seen that, although the room temperature comprehensive mechanical property of embodiment 1 be better than AZ91, but mechanical behavior under high temperature but slightly Surface colors in AZ91.
Embodiment 2
I), alloy is constituted
The 2-in-1 golden chemical composition of embodiment is shown in Table 4.The 2-in-1 golden chemical component table of the embodiment of table 4.（Percentage by weight wt %) mouth ^ Ε aluminium zinc-manganese magnesium
The balance of embodiment 2 6.16 5.08 0.31 0.48
II), alloy smelting and casting
The smelting and casting of reference implementation example 1.Difference is：Both Zn contents are different.
Π Ι), the heat treatment of alloy：
The heat treatment of reference implementation example 1.Difference is：According to the 2-in-1 golden DTA data of embodiment, the temperature of its solution heat treatment is 360 °C, and the time is 12 hours；The temperature of Ageing Treatment is 180 °C, and the time is 16 hours.
), IV Mechanics Performance Testing
The Mechanics Performance Testing of reference implementation example 1.The 2-in-1 golden room-temperature mechanical property yield strength tensile strength elongation percentage ballistic work heat treatment state Brinell hardness of the embodiment of table 5.
(MPa) (MPa) (%) (J) as cast condition 110 210 8 63 15
The contrast situation that T6 is heat-treated the embodiments 2 of 145 250 6 .74 12 and the mechanical behavior under high temperature of AZ91 alloys is shown in Figure 11.As can be seen that not only room temperature comprehensive mechanical property is better than AZ91 to embodiment 2, and mechanical behavior under high temperature is also superior to AZ91.
Embodiment 3
I), alloy is constituted
The chemical composition of the alloy of embodiment 3 is shown in Table 6.The Hua Cheng I of the alloy of 6. embodiment of table 3（Percentage by weight wt %) 3 5.89 6.74 0.35 0.53 balance of alloy aluminum zinc-manganese magnesium embodiment
II), alloy smelting and casting
The smelting and casting of reference implementation example 1.Difference is：Both Zn contents are different.
III), the heat treatment of alloy：
The heat treatment of reference implementation example 1.Difference is:According to the DTA data of the alloy of embodiment 3, the temperature of its solution heat treatment is 350 °C, and the time is 12 hours；The temperature of Ageing Treatment is 180 °C, and the time is 16 hours.
), IV Mechanics Performance Testing
The Mechanics Performance Testing of reference implementation example 1.The room-temperature mechanical property heat treatment state yield strength tensile strength elongation percentage Brinell hardness ballistic work of the alloy of 7. embodiment of table 3
(MPa) (MPa) (%) (J) as cast condition 115 202 6.5 67 13
The contrast situation of the embodiment 3 of T6 heat treatments 153 260 5 77 9 and the mechanical behavior under high temperature of AZ91 alloys is shown in Figure 11.As can be seen that embodiment 3 not only room temperature comprehensive mechanical property be higher than AZ91, and mechanical behavior under high temperature Intensity attribute also superior to AZ91.
Embodiment 4
I), alloy is constituted
The chemical composition of the alloy of embodiment 4 is shown in Table 8.
8. the Hua Cheng Strip of the alloy of embodiment 4（Percentage by weight wt %)
Rich cerium mixing
Aluminium zinc-manganese
Rare earth
The balance of embodiment 4 6.00 3.79 0.54 0.50 0.90
II), alloy smelting and casting
The smelting and casting of reference implementation example 1.Difference is：The alloy of embodiment 4 adds a small amount of cerium-rich mischmetal on the basis of the alloy of embodiment 1.
Because the fusing point of mischmetal is higher, therefore when adding dispensing, first to add cerium-rich mischmetal, and the melt temperature preferably in crucible adds mischmetal when being 750 800 °C.
Π Ι), the heat treatment of alloy：
The heat treatment of reference implementation example 1.Difference is：According to the DTA data of the alloy of embodiment 4, the heat treatment solid solution temperature of alloy is 370 °C, and the time is 12 hours；The temperature of Ageing Treatment is 180 °C, and the time is 16 hours.
IV), Mechanics Performance Testing
The Mechanics Performance Testing of reference implementation example 1.The room-temperature mechanical property yield strength tensile strength elongation percentage ballistic work heat treatment state Brinell hardness of the alloy of embodiment 4
(MPa) (MPa) (%) (J) prays state 111 230 10 64 19
T6 heat treatments 146 272 8.7 77 13
The contrast situation of embodiment 4 and the mechanical behavior under high temperature of AZ91 alloys is shown in Figure 12.It can be seen that, although the room temperature comprehensive mechanical property of embodiment 1 be better than AZ91, but mechanical behavior under high temperature but slightly Attack colors in AZ91.
Embodiment 5
I), alloy is constituted
The chemical composition of the alloy of embodiment 5 is shown in Table 10.The chemistry of the alloy of 10. embodiment of table 5 is into ^ (percentage by weight wt %)
Rich cerium mixing
Alloy aluminum zinc-manganese
Rare earth
The balance of embodiment 5 4.77 5.59 0.42 0.45 0.49
II), alloy smelting and casting
The smelting and casting of reference implementation example 1.Difference is：The smelting and casting of reference implementation example 1.Difference is：In addition to aluminium, Zn content are different, a small amount of cerium-rich mischmetal is also added into the alloy of embodiment 5.
Because the fusing point of mischmetal is higher, therefore when adding dispensing, first to add cerium-rich mischmetal, and the melt temperature preferably in crucible adds mischmetal when being 750 800 °C.
III), the heat treatment of alloy：
The heat treatment of reference implementation example 1.Difference is：According to the DTA data of the alloy of embodiment 5, the heat treatment solid solution temperature of alloy is 350 °C, and the time is 12 hours；The temperature of Ageing Treatment is 180 °C, and the time is 16 hours.
W Mechanics Performance Testings
The Mechanics Performance Testing of reference implementation example 1.The room-temperature mechanical property yield strength tensile strength elongation percentage ballistic work heat treatment state Brinell hardness of the alloy of 11 embodiment of table 5
(MPa) (MPa) (%) (J) as cast condition 115 210 7.4 68 15
The contrast situation of the embodiment 5 of T6 heat treatments 156 282 7.0 79 12 and the mechanical behavior under high temperature of AZ91 alloys is shown in Figure 12.As can be seen that embodiment 5 not only room temperature comprehensive mechanical property be better than AZ91, and mechanical behavior under high temperature Intensity attribute also superior to AZ91.
Claims (1)
- Claim1st, a kind of high-intensity high-tenacity cast magnesium alloy, it is characterised in that：By weight percentage, the essential element composition for alloying is as follows：Aluminium content is 3 ~ 9%；Zn content is 3.5 ~ 9%；Manganese content is 0.15 ~ 1.0%；Antimony content is 0.01-2%；Content of magnesium is balance.2nd, ^^ gold is cast according to the high just property of the high intensity described in claim 1, it is characterised in that：Households M antimony powders can be technical pure antimony, and its purity is 99.7%.3rd, ^^ gold is cast according to the high Wei Ren of high intensity described in claim 1, it is characterised in that：0 ~ 2 wt% cerium-rich mischmetal, calcium, certain element of silicon thrin can also further be contained in alloy.4th, the preparation method of ^ ^ gold is cast according to the high-intensity high-tenacity described in claim 1, it is characterised in that its melting and as follows around note process： . .1) crucible target temperature is first set as 700 ~ 750 °C, is begun to warm up；Then various dispensings are put and is preheated to 140 ~ 200 °C in an oven, and the coverture for accounting for purpose alloy gross weight 0.64% is put into baking in baking oven；In addition, casting is preheated into 20 (00 °C with mould in other batch-type furnace；2) when crucible is warming up to 280 ~ 320 °C, it is passed through C02Gas displacement is carried out in gas to crucible, the Λ 30% 50% above-mentioned coverture toasted is then added in crucible bottom, then afterwards by preheated pure magnesium dispensing side crucible；3) pure magnesium dispensing melts and waits crucible temperature stable after 700 ~ 750 °C, sequentially adds the various dispensings of preheating from high to low according to fusing point, then melt is stirred 8 ~ 10 minutes；During this, the remaining coverture toasted is added, is defined so that surface is non-ignitable；4) crucible temperature is stable after 700 ~ 750 °C, and melt stands 4 ~ 6 minutes, by percent by volume, in 99 99.5% air or C02+ 0.5-1% SF6Surface scum is drawn out under mixed body protection；5) draw after slag finishes, crucible temperature is maintained at 700 ~ 750 °C, by percent by volume, in 99 ~ 99.5% air or C02+ 0.5-1% SF6Mixed gas protected lower cast molding.5th, ^ Preparation Methods are closed according to the high-intensity high-tenacity casting magnesium described in claim 4, it is characterised in that：The heat treatment that alloy is used is segmented into three kinds：Solution treatment, artificial aging and solution treatment+artificial aging.6th, according to the preparation method of the high-intensity high-tenacity cast magnesium alloy described in claim 5, it is characterised in that：The temperature range of the solution treatment is that 34 (K400 °C, time of solution treatment is 8 ~ 24 hours.7th, according to the preparation method of the high Firmware cast magnesium alloys of high intensity described in claim 5, it is characterised in that：The temperature range of the artificial aging is 70 ~ 200 °C, and the time of processing is 8 ~ 24 hours.8th, according to the preparation method of the high-intensity high-tenacity cast magnesium alloy described in claim 5, it is characterised in that：The cast molding is prayed using metal mold makes, or using sand casting, compression casting or Extrution casting technique.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100205671A CN100338250C (en) | 2004-05-19 | 2004-05-19 | High strength and high toughness cast magnesium alloy and preparing process thereof |
| CN200410020567.1 | 2004-05-19 | ||
| PCT/CN2005/000479 WO2005111251A1 (en) | 2004-05-19 | 2005-04-11 | A high-strength, high-toughness cast magnesium alloy and the method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1938441A true CN1938441A (en) | 2007-03-28 |
| CN100408709C CN100408709C (en) | 2008-08-06 |
Family
ID=35394170
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004100205671A Expired - Fee Related CN100338250C (en) | 2004-05-19 | 2004-05-19 | High strength and high toughness cast magnesium alloy and preparing process thereof |
| CNB2005800098757A Expired - Fee Related CN100408709C (en) | 2004-05-19 | 2005-04-11 | High-strength-toughness magnesium alloy and its preparing method |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004100205671A Expired - Fee Related CN100338250C (en) | 2004-05-19 | 2004-05-19 | High strength and high toughness cast magnesium alloy and preparing process thereof |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US20090068053A1 (en) |
| CN (2) | CN100338250C (en) |
| WO (1) | WO2005111251A1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102242299A (en) * | 2011-07-26 | 2011-11-16 | 中国科学院金属研究所 | Bi and Nd composite reinforced high-strength cast magnesium alloy and preparation method thereof |
| CN108085549A (en) * | 2017-12-27 | 2018-05-29 | 哈尔滨理工大学 | A kind of method that ultrasonic wave auxiliary mechanical agitation prepares new magnesium-based composite material |
| CN110157929A (en) * | 2019-04-30 | 2019-08-23 | 西安交通大学 | Mg in a kind of improvement magnesium alloy2The method of Si reinforcing phase constitution and pattern |
| CN114836663A (en) * | 2022-05-31 | 2022-08-02 | 重庆大学 | High-strength cast magnesium alloy and preparation method thereof |
Families Citing this family (47)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100406159C (en) * | 2006-01-20 | 2008-07-30 | 中国科学院金属研究所 | Method for casting Mg-Al-Zn based magnesium alloy with high strength and high tenacity |
| AT503854B1 (en) * | 2006-05-19 | 2008-01-15 | Arc Leichtmetallkompetenzzentrum Ranshofen Gmbh | MAGNESIUM-BASED ALLOY |
| CN100432258C (en) * | 2006-11-01 | 2008-11-12 | 中国科学院金属研究所 | Quasi crystal phase fortified magnesium lithium alloy and its preparation method |
| DE102008037200B4 (en) * | 2008-08-11 | 2015-07-09 | Aap Implantate Ag | Use of a die-casting method for producing a magnesium implant and magnesium alloy |
| CN102108464B (en) * | 2009-12-23 | 2013-01-30 | 中国科学院金属研究所 | Anticorrosion magnesium alloy |
| CN101880845A (en) * | 2010-06-11 | 2010-11-10 | 燕山大学 | Method for thinning AM60B cast magnesium alloy grains |
| CN102764876A (en) * | 2011-05-03 | 2012-11-07 | 远轻铝业（中国）有限公司 | Gravity casting process of back cover board of turbosupercharger |
| CN102321859A (en) * | 2011-08-31 | 2012-01-18 | 燕山大学 | A kind of method of AZ91D cast magnesium alloy grains |
| CN102994847B (en) * | 2011-09-09 | 2015-01-07 | 江汉大学 | Heatproof magnesium alloy |
| CN102994835B (en) * | 2011-09-09 | 2015-01-07 | 江汉大学 | Heatproof magnesium alloy |
| CN102517489B (en) * | 2011-12-20 | 2013-06-19 | 内蒙古五二特种材料工程技术研究中心 | Method for preparing Mg2Si/Mg composites by recovered silicon powder |
| CN102632822A (en) * | 2012-03-31 | 2012-08-15 | 北京华盛荣镁业科技有限公司 | Passenger car seat frame, manufacturing method thereof and passenger car seat |
| CN102626779A (en) * | 2012-04-25 | 2012-08-08 | 辽宁工业大学 | Method for preparing magnesium alloy ingot and solidification system |
| CN103305735B (en) * | 2013-06-24 | 2015-03-11 | 山东富通电气有限公司 | Reinforced magnesium alloy and preparation method thereof |
| CN103388095B (en) * | 2013-07-18 | 2016-10-26 | 上海交通大学 | Mg-Gd-Y-Zr series magnesium alloy and the heat treatment method of large-scaled complex castings thereof |
| CN103643064B (en) * | 2013-12-25 | 2015-09-16 | 昆明理工大学 | The method of the magnesium alloy gradient material that a kind of LPSO of preparation phase strengthens |
| CN103695745B (en) * | 2014-01-16 | 2015-07-29 | 徐茂航 | A kind of boron nitride strengthens magnesium alloy and preparation method thereof |
| CN104032196B (en) * | 2014-06-25 | 2015-12-02 | 河北镁轮镁合金科技有限公司 | high-strength magnesium alloy material and preparation method thereof |
| CN104328317B (en) * | 2014-11-26 | 2016-08-24 | 衢州市联橙环保科技有限公司 | A kind of magnesium-rare earth and manufacture craft thereof |
| CN104561709B (en) * | 2014-12-04 | 2017-05-17 | 沈阳工业大学 | High-creep-performance casting magnesium alloy and preparation method thereof |
| CN104630584A (en) * | 2015-02-03 | 2015-05-20 | 闻喜县瑞格镁业有限公司 | Magnesium alloy for high-fluidity high-strength ultrathin-wall component and preparation method of magnesium alloy |
| DE102015109775B3 (en) | 2015-06-18 | 2016-09-22 | RobArt GmbH | Optical triangulation sensor for distance measurement |
| CN105039816B (en) * | 2015-07-20 | 2017-05-31 | 河南科技大学 | A kind of high strength and low cost heat resistance magnesium alloy and preparation method thereof |
| CN105522866A (en) * | 2015-12-15 | 2016-04-27 | 苏州爱盟机械有限公司 | Vehicle hub |
| CN106591612A (en) * | 2016-11-08 | 2017-04-26 | 中航装甲科技有限公司 | Preparation method of composite armour material and stirring device for preparing armour material |
| CN106513630A (en) * | 2016-11-10 | 2017-03-22 | 无锡市明盛强力风机有限公司 | Extrusion casting technology for magnesium alloy hub |
| CN107099685B (en) * | 2017-04-29 | 2018-11-09 | 太原科技大学 | A kind of preparation method of high-strength and high-ductility fast degradation magnesium alloy |
| CN107760948A (en) * | 2017-10-24 | 2018-03-06 | 西科创新（深圳）科技有限公司 | A kind of magnesium alloy material luggage case and its manufacturing process |
| CN107964603B (en) * | 2017-11-24 | 2019-06-25 | 湖北工业大学 | A kind of synthetic method of Mg (Zn)-MgSb intermetallic compound structure material |
| CN108004423A (en) * | 2017-11-30 | 2018-05-08 | 于海松 | The synthesis technique of high-performance magnesium base alloy |
| CN108103334A (en) * | 2017-12-28 | 2018-06-01 | 重庆仟和镁业科技有限公司 | The production technology of whole magnesium alloy battery case |
| CN108642357B (en) * | 2018-07-11 | 2019-12-06 | 上海交通大学 | Nd-containing cast ultralight high-strength magnesium-lithium alloy and preparation method thereof |
| CN108977710B (en) * | 2018-07-23 | 2020-11-17 | 上海交通大学 | Extrusion casting magnesium alloy material and preparation method thereof |
| CN108977711B (en) * | 2018-07-23 | 2020-11-17 | 上海交通大学 | Die-casting magnesium alloy material and preparation method thereof |
| CN109084008A (en) * | 2018-08-27 | 2018-12-25 | 重庆元和利泰镁合金制造有限公司 | Magnesium alloy gear box casing and preparation method thereof |
| CN109022979A (en) * | 2018-09-10 | 2018-12-18 | 江苏理工学院 | A kind of high-strength temperature-resistant Mg-Zn-Al-Y-Sb magnesium alloy and preparation method thereof |
| CN109182857B (en) * | 2018-11-08 | 2024-01-30 | 中信戴卡股份有限公司 | High-strength and high-toughness deformed magnesium alloy and preparation method thereof |
| CN109943757B (en) * | 2019-03-29 | 2021-07-20 | 上海交通大学 | High-strength-toughness heat-resistant Mg-Y-Er alloy suitable for low-pressure casting and preparation method thereof |
| CN110029257A (en) * | 2019-04-23 | 2019-07-19 | 安徽双巨电器有限公司 | A kind of aluminium shell of capacitor material and preparation method thereof |
| GB2583482A (en) | 2019-04-29 | 2020-11-04 | Univ Brunel | A casting magnesium alloy for providing improved thermal conductivity |
| CN110373559A (en) * | 2019-08-26 | 2019-10-25 | 上海交通大学 | A kind of method of suitable magnesium and magnesium alloy smelting and casting |
| CN110438373B (en) * | 2019-08-29 | 2020-07-10 | 东北大学 | Preparation method of magnesium-based composite material |
| CN114540687B (en) * | 2021-12-16 | 2022-11-25 | 中信戴卡股份有限公司 | Magnesium alloy, preparation method thereof and process for preparing wheel by using magnesium alloy |
| CN114540681B (en) * | 2021-12-29 | 2022-10-25 | 北京理工大学 | High-strength high-modulus corrosion-resistant dual-phase magnesium-lithium alloy structural member and preparation method thereof |
| CN115029594A (en) * | 2022-06-20 | 2022-09-09 | 重庆大学 | Wrought magnesium alloy and preparation method thereof |
| CN115874098A (en) * | 2022-12-05 | 2023-03-31 | 中国科学院长春应用化学研究所 | Mg-Al-RE-Zn-Ca-Mn rare earth magnesium alloy and preparation method thereof |
| CN115976384B (en) * | 2022-12-30 | 2024-02-23 | 重庆大学 | AlN/AE44 composite material with excellent high-temperature mechanical property and preparation method thereof |
Family Cites Families (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2314852A (en) * | 1940-09-09 | 1943-03-23 | Anglo California Nat Bank Of S | Heat treatment of magnesium base alloys |
| US3119725A (en) * | 1961-11-27 | 1964-01-28 | Dow Chemical Co | Die-expressed article of magnesium-base alloy and method of making |
| US4675157A (en) * | 1984-06-07 | 1987-06-23 | Allied Corporation | High strength rapidly solidified magnesium base metal alloys |
| CN1127306A (en) * | 1994-07-12 | 1996-07-24 | 宇部兴产株式会社 | Creep-resisting, corrosion-resisting magnesium alloy |
| US5855697A (en) * | 1997-05-21 | 1999-01-05 | Imra America, Inc. | Magnesium alloy having superior elevated-temperature properties and die castability |
| JP3898302B2 (en) * | 1997-10-03 | 2007-03-28 | 日本パーカライジング株式会社 | Surface treatment agent composition for metal material and treatment method |
| IL125681A (en) * | 1998-08-06 | 2001-06-14 | Dead Sea Magnesium Ltd | Magnesium alloy for high temperature applications |
| JP3603706B2 (en) * | 1999-12-03 | 2004-12-22 | 株式会社日立製作所 | High-strength Mg-based alloys and Mg-based cast alloys and articles |
| KR20020078936A (en) * | 2001-04-11 | 2002-10-19 | 학교법인연세대학교 | Quasicrystalline phase hardened Mg-based metallic alloy exhibiting warm and hot formability |
| CN1168840C (en) * | 2001-08-14 | 2004-09-29 | 上海交通大学 | Multicomponent heat-resistant magnesium alloy for car and its founding process |
| CN1169988C (en) * | 2001-08-22 | 2004-10-06 | 东南大学 | Low cost heat-resistant magnesium alloy |
| CN1203202C (en) * | 2002-10-17 | 2005-05-25 | 山西至诚科技有限公司 | Preparation method of magnesium alloy |
| JP2004263280A (en) * | 2003-03-04 | 2004-09-24 | Toyota Central Res & Dev Lab Inc | Corrosionproof magnesium alloy member, corrosionproofing treatment method for magnesium alloy member, and corrosionproofing method for magnesium alloy member |
| CN1488773A (en) * | 2003-09-05 | 2004-04-14 | 郑州大学 | Rare-earth-containg high-zinc-magnesium alloy and preparing method thereof |
-
2004
- 2004-05-19 CN CNB2004100205671A patent/CN100338250C/en not_active Expired - Fee Related
-
2005
- 2005-04-11 WO PCT/CN2005/000479 patent/WO2005111251A1/en active Application Filing
- 2005-04-11 CN CNB2005800098757A patent/CN100408709C/en not_active Expired - Fee Related
- 2005-04-11 US US10/582,541 patent/US20090068053A1/en not_active Abandoned
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102242299A (en) * | 2011-07-26 | 2011-11-16 | 中国科学院金属研究所 | Bi and Nd composite reinforced high-strength cast magnesium alloy and preparation method thereof |
| CN108085549A (en) * | 2017-12-27 | 2018-05-29 | 哈尔滨理工大学 | A kind of method that ultrasonic wave auxiliary mechanical agitation prepares new magnesium-based composite material |
| CN110157929A (en) * | 2019-04-30 | 2019-08-23 | 西安交通大学 | Mg in a kind of improvement magnesium alloy2The method of Si reinforcing phase constitution and pattern |
| CN114836663A (en) * | 2022-05-31 | 2022-08-02 | 重庆大学 | High-strength cast magnesium alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100408709C (en) | 2008-08-06 |
| WO2005111251A1 (en) | 2005-11-24 |
| US20090068053A1 (en) | 2009-03-12 |
| WO2005111251A8 (en) | 2006-03-02 |
| CN100338250C (en) | 2007-09-19 |
| CN1699612A (en) | 2005-11-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1938441A (en) | High-strength-toughness magnesium alloy and its preparing method | |
| Czerwinski | Cerium in aluminum alloys | |
| CN102230118B (en) | Magnesium alloy of high intensity and high yield ratio and preparation method thereof | |
| Ji et al. | Development of a super ductile diecast Al–Mg–Si alloy | |
| RU2213796C2 (en) | High-temperature magnesium alloy | |
| Liu et al. | The solidification process of Al–Mg–Si alloys | |
| CN106609331B (en) | High-ductility diecast magnesium alloy and its manufacturing process | |
| CN102618760B (en) | MgAlZn series heat resistant magnesium alloy containing niobium | |
| CN102676887A (en) | Aluminum alloy for compression casting and casting of aluminum alloy | |
| CN109487107B (en) | Composite modifier for cast aluminum alloy with iron-rich phase modification and modification method thereof | |
| WO2011090451A1 (en) | CASTING ALLOY OF THE AIMgSI TYPE | |
| EP2481822A1 (en) | Magnesium-aluminum based alloy with grain refiner | |
| CA3065136C (en) | High-strength aluminium-based alloy | |
| CN101775529A (en) | High-strength cast aluminum-silicon alloy for engine body and preparation method thereof | |
| WO2010056130A1 (en) | Magnesium based alloys and processes for preparation thereof | |
| CN102618757A (en) | Heat-resistant magnesium alloy | |
| CN102618762A (en) | Heat-resisting magnesium alloy | |
| CN101876018A (en) | High-strength casting aluminium-silicon alloy for piston and preparation method thereof | |
| JP2004162090A (en) | Heat resistant magnesium alloy | |
| CN101818293B (en) | Heat resistant magnesium alloy | |
| Hanwu et al. | Preparation and characterization of Mg-6Li and Mg-6Li-1Y alloys | |
| CN105154733A (en) | Novel non-rare earth cast magnesium alloy and preparation method thereof | |
| CN115418535B (en) | Aluminum alloy material, preparation method and application thereof, and aluminum alloy product | |
| CN103966494A (en) | Highly heat-resistant magnalium containing calcium and rare earth | |
| Guangyin et al. | Mechanical properties and microstructure of Mg-Al-Zn-Si-base alloy |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20080806 Termination date: 20160411 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |