CN101952467A - High-strength aluminum casting alloys resistant to hot tearing - Google Patents

High-strength aluminum casting alloys resistant to hot tearing Download PDF

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CN101952467A
CN101952467A CN2009801026580A CN200980102658A CN101952467A CN 101952467 A CN101952467 A CN 101952467A CN 2009801026580 A CN2009801026580 A CN 2009801026580A CN 200980102658 A CN200980102658 A CN 200980102658A CN 101952467 A CN101952467 A CN 101952467A
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crystal grain
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阿输迦·米斯拉
查尔斯·库埃曼
周恒正
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Questek Innovations LLC
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc 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
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent

Abstract

An aluminum casting alloy resistant to hot tearing includes, in wt%, about 4.0 to about 6.9 Zn, about 2.0 to about 3.5 Mg, about 0.6 to about 1.2 Cu, about 0.38 to about 0.57 Sc, about 0.18 to about 0.28 Zr, and the balance Al and impurities, substantially excluding Fe, Mn, and Si, said alloy characterized by a freezing range of less than about 150 DEG C, solidus temperature above about 490 DEG C, and eutectic phase fraction above about 5% at the late stages of solidification. The alloy is processed to form a dispersion of L12 particles inoculating fcc grains with a grain diameter of about 40 to about 60 [mu]m, and Eta'-phase precipitates enabling an ambient yield strength from about 410 MPa to about 540 MPa.

Description

The high strength cast aluminum alloys that heat resistanceheat resistant is split
Governmental interests
The activity of relevant theme of the present invention progress obtains United States Government at least and partly supports, and therefore, may obtain U.S.'s license or other rights, and concrete contract number is FA8650-05-C-5800.
Background technology
7XXX wrought alloys based on Al-Zn is generally used for requiring in the building operation of high strength coefficient.Because the nearly net shape products of castings production, it is compared with wrought alloys, has reduced cost and corresponding time of delivery in later stage.Yet known 7XXX alloy is easily hot tearing in process of setting, because of rather than best cast material.Hot tearing is that the significant difference owing to high relatively thermal expansivity and liquid and solid volume causes.
United States Patent (USP) 7,060,139 (at this as a reference) disclose a kind of aldural, and it consists of (wt%): Al-6.0～12.0Zn-2.0～3.5Mg-0.1～0.5Sc-0.05～0.20Zr-0.5～3.0Cu-0.10～0.45Mg-0.08～0.35Fe-0.07～0.20Si.The aluminium alloy of this patent disclosure has high tensile strength, and reaches maintenance high-elongation under the low temperature at ambient temperature.The freezing range of the aluminium alloy of this patent disclosure is about 164-195 ℃, and solidus temperature is about 422-466 ℃, and the eutectic phase composition is about 1.1-1.5%.Yet, this aluminium alloy casting poor performance.Therefore, but the 7XXX cast aluminium alloy that needs a kind of new heat resistanceheat resistant to split.Such alloy can be used in production articles for use such as hydrogen turbopump shell or other the aeronautical material.
Summary of the invention
The present invention mainly comprises the high strength cast aluminum alloys that a kind of heat resistanceheat resistant is split.The yield strength of this casting alloy at room temperature is about 410MPa-540MPa.Alloy of the present invention is based on Al-Zn's, and its main alloying constituent is Sc, Zr, Mg and Cu.The amount optimization of Sr and Zr is to produce elementary L1 2The phase particle, this particle refining grain size number, and ability, fatigue performance and toughness are split in the raising heat resistanceheat resistant.Fe, the amount of Mn and Si keeps minimum level, splits ability because these compositions are unfavorable for intensity and heat resistanceheat resistant.For producing elementary L1 2The phase particle, L1 2The solvus temperature of phase must be more than the solvus temperature of fcc (face-centered cubic) phase.The solvus temperature can be utilized the thermodynamic data storehouse or calculate bag, as
Figure BPA00001184699800011
Software provides
Figure BPA00001184699800012
Version calculates.Perhaps, in the composition space of alloy, the solvus temperature approaches following equation:
L1 2Solvus temperature=87.01 * wp Sc+ 157.89 * wp Zr-
243.43×wp Sc×wp Zr+267.06×wp Sc 0.14+769.51×wp Zr 0.05
Fcc solvus temperature=-1.76 * wp Zn-5.14 * wp Mg-
0.005×wp Zn×wp Mg+139.13×wp Zn 0.002+792.11×wp Mg 0.0002
Wherein, wp Sc, wp Zr, wp Zn, wp MgBe respectively Sc, Zr, Zn, the weight percentage of Mg.These equatioies are based on the best-fit of solvus temperature.
In addition, the content of Zr is maintained at about below the 0.3wt% to form the minimum D0 that has 23The Al of crystalline structure 3Zr.As Hyde[Hyde, Addition of Scandium to Aerospace Casting Alloys.Ph.D.diss. K.2001.The, University of Manchester (as a reference) at this] described Al-0.5Sc-0.4Zr (wt%), D0 23Particle increases fast, too huge and effective refining fcc grain size number.These disclosed alloys adopt to have L1 in melt cools 2The little Al of crystalline structure 3(Sc, Zr) particle is to breed the little crystal grain of fcc.Because at L1 2In, Zr is the cheap alternative of Sc, the alloy among the present invention uses Zr as much as possible, is about 0.25 ± 0.05wt%.Yet, when cost is not limiting factor, can be used in combination and only be the Zr of 0.15wt% and relatively large Sc.
The amount optimization of Sc and Zr in the casting alloy is to be suitable for the speed of cooling of about 100 ℃ of per seconds.L1 2-Al 3(Sc, Zr) particle size distribution depends on the melt speed of cooling.Being casted into Sha Mo makes speed of cooling be about 0.5 ℃ of per second.For example when steel billet is used water cooling in the process of setting, can reach higher speed of cooling by the direct chill casting casting.100 ℃ of above speed of cooling of per second can reach by castmethod such as CRP (Continuous Rheoconversion Process, rheology conversion process continuously).
As shown in Figure 1, big elementary L1 2Particle will make the diameter of fcc crystal grain greater than 200 μ m.For making when speed of cooling reaches 100 ℃ of per seconds, the diameter of fcc crystal grain is 40-60 μ m, elementary L1 2The mean radius of particle should be less than 2 μ m, and its phase composition should be lower than 1wt%.Figure 1A is for making L1 2Sc when particle reaches the requirement size and the amount of Zr.Because the amount of Zr keeps below 0.3wt%, therefore, the amount of Sc is maintained at about more than the 0.4wt%, reaches about 0.6wt%.
Owing to hot tearing is actually because the thermal contraction when solidifying causes, therefore, can improves heat resistanceheat resistant by the mode that reduces the freezing range and increase aluminium alloy the solidus temperature more than the solidus temperature be entirely solid the time and split ability.Be increased in and solidify eutectic phase composition that the later stage forms and also help improving heat resistanceheat resistant and split ability, because eutectic phase solidifies fully a temperature, and eutectic phase is reduced in the melt shrinkage of freezing range.
Solidifying parameter such as freezing range, solidus temperature and eutectic phase composition can or calculate bag by the thermodynamic data storehouse, draws as the Thermo-Calc computed in software.Be the parameter of solidifying of the alloy system that utilizes Thermo-Calc computed in software complexity, gibbs (Gibbs) free energy of relevant phase must pass through CALPHAD (CALculation of PHAse Diagrams, calphad) method to be evaluated.Such being correlated with is meta η ' phase mutually, strengthens because the 7XXX wrought alloys adopts η ' to precipitate mutually.Strengthen for high-level efficiency, the sedimentary mean radius of η ' should be less than about 5nm.
After having evaluated thermodynamics, can utilize QuesTek Innovations LLC company to provide
Figure BPA00001184699800021
Software 0.9.2 version simulation η ' phase precipitation kinetics.The particle size distribution of prediction can be as the input data of yield strength mechanical model, and it comprises precipitation strength, the contribution that grain size number is strengthened, sosoloid is strengthened and dislocation is strengthened.The amount of Zn, Mg and Cu is the parameter optimization of solidifying that makes in different yield strength levels in the alloy.
The amount of Fe, Mn and Si is low as much as possible, because these become branch to form Al 13Fe 4, Al 7Cu 2Fe, Mg 2Si, Al 6The insoluble composition particle that Mn etc. are big, these particles can have negative impact to toughness, fatigue strength and SCC resistance.Preferably, the amount of Fe is lower than 0.0075wt%, and Mn is lower than 0.2wt%, and Si is lower than 0.03wt%.
For prevent homogenize or the solutionizing treating processes in incipient melting, homogenize or temperature that solutionizing is handled should be lower than final temperature of solidification, preferably, have safety coefficient and be about 10-30 ℃.As shown in Figure 3, solutionizing is handled and the two steps processing that homogenizes and distinguish, can be introduced extra safety coefficient to prevent incipient melting.The final temperature of solidification that calculates is 493 ℃.Therefore, in one embodiment, homogenize and solutionizing handle should be at about 460-480 ℃.Such treatment time should be divided coagulation phenomena to eliminate most of rough casting by sufficiently long.As shown in Figure 4, the simulation that homogenizes shows, 460 ℃ homogenized 2 hours after, 480 ℃ of solutionizing were handled 1 hour, should enough eliminate most of rough casting and divide coagulation phenomena.The kinetics software DICTRA that is provided by Thermo-Cal software can be provided in this simulation TM(DIffusion ControlledTRAnsformations) version 24 is operated.
The present invention can use the 7XXX aluminium alloy, but the invention is not restricted to this.Therefore, a beneficial effect of the present invention is the hot tearing of eliminating or eliminate substantially cast aluminium alloy.
Below describe beneficial effect of the present invention, advantage and feature in detail.
Description of drawings
Describe the present invention in detail below with reference to Figure of description:
Figure 1A and 1B are respectively alloy Sc and Zr simulates initial L1 2The synoptic diagram of particle radii and simulation grain size number;
Fig. 2 A, 2B and 2C are respectively the intensity of Zn, Mg and Cu content and solidify the parameter level line, wherein, have used following legend:
_ _ _ _ _ _ _ _ _ _ _ _ yield strength iso level line (ksi)
Figure BPA00001184699800031
Eutectic % (Scheil)
The Scheil freezing range (℃)
_ _ _ _ _ _ _ _ _ _ _ _ _ the Scheil temperature of solidification (℃)
Star: high strength solution (YS～80ksi)
Trilateral: middle intensity solution (YS～70ksi)
Square: low strength solution (YS～60ksi)
Fig. 3 is the time-hygrogram of one embodiment of the invention interalloy procedure of processing;
Fig. 4 is the simulation that homogenizes of one embodiment of the invention;
Fig. 5 is the Photomicrograph of alloy A of the present invention; It is a symbolic Photomicrograph of the embodiment of the invention.
Embodiment
Below be specific embodiments of the invention.
Embodiment 1: alloy A
Preparation comprises the melt of Al-6.3Zn-3.2Mg-1.1Cu-0.52Sc-0.20Zr (wt%).It is that mean value adds deduct 10% that typical alloy preferred component changes difference.Alloy is cast with 50～100 ℃/s speed of cooling of actual measurement to the sand-cast mould by the CRP reactor.As shown in Figure 3, optimum processing condition are to adopt heat and other static pressuring processes, and 460 ℃ homogenized 2 hours, and water quenching is used in 480 ℃ of solution treatment 1 hour, is positioned over room temperature 24h, 120 ± 10 ℃ of aging 20h.Room temperature yield strength under this condition is 521 ± 12MPa.Crystal grain diameter is about 50 μ m, or ASTM (American Society forTesting and Materials, the U.S. is detected and the materialogy meeting) the crystal grain number of degrees are about 5.7.The freezing range that calculates is 136 ℃, and solidus temperature is 493 ℃, is 10% at the eutectic phase composition that solidifies later stage formation.
The rectangular plate of alloy A is cast fully and is not had hot tearing.Melt utilizes argon gas at 700-720 ℃ of degasification 45min, pours into a mould preceding 740 ℃ then and reheats.The dark 1cm of mould.Watering the time of filling with mould is about 20 seconds.Mould fully fills up, and produces the panel that is fit to mould.After coming off from mould, remove all gatings and cleaning thing, panel is transported to UES, and (Wright Patterson Air Force Base) moulds in Lai Te-Paterson base air depot in Inc. company.Fig. 5 is the microstructure of alloy A, the hole of foundry goods, typical L1 2Particle and eutectic phase are used a, b and c mark respectively.
Embodiment 2: alloy B
Preparation comprises the melt of Al-5.3Zn-3.0Mg-1.1Cu-0.55Sc-0.25Zr (wt%).It is that mean value adds deduct 10% that typical alloy preferred component changes difference.Alloy is cast with the 100 ℃/s speed of cooling of actual measurement to the sand-cast mould by the CRP reactor.As shown in Figure 3, optimum processing condition are to adopt heat and other static pressuring processes, and 460 ℃ homogenized 2 hours, and water quenching use in 480 ℃ of solution treatment 1 hour, is positioned over room temperature 24 hours, and 120 ± 10 ℃ were worn out 20 hours.Room temperature yield strength under this condition is 482 ± 6MPa.Crystal grain diameter is about 54 μ m, or the ASTM crystal grain number of degrees are about 5.5.The freezing range that calculates is 139 ℃, and solidus temperature is 494 ℃, is 9% at the eutectic phase composition that solidifies later stage formation.The rectangular plate of alloy B is cast fully and do not had hot tearing, and is consistent with alloy A or unanimous on the whole.
Embodiment 3: alloy C
Preparation comprises the melt of Al-4.5Zn-2.3Mg-0.62Cu-0.42Sc-0.25Zr (wt%).It is that mean value adds deduct 10% that typical alloy preferred component changes difference.Alloy is cast to the sand-cast mould by the CRP reactor.As shown in Figure 3, optimum processing condition are to adopt heat and other static pressuring processes, 460 ℃ of 2h that homogenize, and water quenching use in 480 ℃ of solution treatment 1 hour, is positioned over room temperature 24 hours, and 120 ± 10 ℃ were worn out 15 hours.Room temperature yield strength under this condition is 410 ± 40MPa.Crystal grain diameter is about 50 μ m, or the ASTM crystal grain number of degrees are about 5.7.The freezing range that calculates is 145 ℃, and solidus temperature is 494 ℃, is 6% at the eutectic phase composition that solidifies later stage formation.Two boards one stove of alloy C is cast fully and do not had hot tearing, and is consistent with alloy A or unanimous on the whole.
Table 1 has been summed up the chemical constitution of the foregoing description and has been realized the general range (in weight percentage) of composition of the present invention:
Table 1
Table 2 has been summed up the foregoing description based on microstructural information and realize the relevant range (in weight percentage) of composition of the present invention:
Table 2
Figure BPA00001184699800052
Embodiments of the invention only are used to illustrate the present invention, limit the scope of the invention and be not used in.Protection scope of the present invention limits by claims.

Claims (10)

1. cast aluminium alloy with heat crack resistance, it is characterized in that, in weight percentage, comprise Zn: about 4.0-6.9%, Mg: about 2.0-3.5%, Cu: about 0.6-1.2%, Sc: about 0.38-0.57%, Zr: about 0.18-0.28%, surplus is Al and impurity, substantially do not contain Fe, Mn and Si, described alloy is: breed the L1 that fcc crystal grain is arranged 2Particle dispersion precipitates mutually with η '.
2. alloy according to claim 1 is characterized in that the average crystal grain diameter of described fcc crystal grain is about 40-60 μ m.
3. alloy according to claim 1 is characterized in that, the mutually sedimentary mean radius of described η ' is less than about 5nm.
4. alloy according to claim 1 is characterized in that, in weight percentage, comprises being lower than about 0.0075% Fe, is lower than about 0.2% Mn and is lower than about 0.03% Si.
5. alloy according to claim 1 is characterized in that, in weight percentage, comprises following composition: about Zn:5.8-6.8%, Mg:2.9-3.5%, Cu:1.0-1.2%, Sc:0.52%, Zr:0.20%.
6. alloy according to claim 1 is characterized in that, in weight percentage, comprises following composition: about Zn:4.8-5.8%, Mg:2.7-3.3%, Cu:1.0-1.2%, Sc:0.55%, Zr:0.25%.
7. alloy according to claim 1 is characterized in that, in weight percentage, comprises following composition: about Zn:4.0-5.0%, Mg:2.0-2.6%, Cu:0.52-0.72%, Sc:0.42%, Zr:0.25%.
8. cast aluminium alloy with heat crack resistance, it is characterized in that, in weight percentage, comprise Zn: about 4.0-6.9%, Mg: about 2.0-3.5%, Cu: about 0.6-1.2%, Sc: about 0.38-0.57%, Zr: about 0.18-0.28%, surplus is Al and impurity, substantially do not comprise Fe, Mn and Si, described alloy is: the freezing range is lower than about 150 ℃, solidus temperature and is higher than about 490 ℃ and solidify eutectic phase composition that the later stage forms greater than about 5%.
9. cast aluminium alloy with heat crack resistance, it is characterized in that, in weight percentage, comprise Zn: about 4.0-6.9%, Mg: about 2.0-3.5%, Cu: about 0.6-1.2%, Sc: about 0.38-0.57%, Zr: about 0.18-0.28%, surplus is Al and impurity, basically do not comprise Fe, Mn and Si, the characteristic of described alloy is: the freezing range be lower than 150 ℃, solidus temperature be higher than 490 ℃, solidify eutectic phase composition that the later stage forms greater than about 5%, breed fcc crystalline L1 arranged 2Particle dispersion and η ' precipitate mutually.
10. cast aluminium alloy with heat crack resistance, it is characterized in that, in weight percentage, comprise Zn: about 4.0-6.9%, Mg: about 2.0-3.5%, Cu: about 0.6-1.2%, Sc: about 0.38-0.57%, Zr: about 0.18-0.28%, surplus is Al and impurity, basically do not comprise Fe, Mn and Si, described alloy is: the freezing range be lower than about 150 ℃, solidus temperature be higher than about 490 ℃, solidify eutectic phase composition that the later stage forms greater than about 5%, breed that diameter is arranged is the L1 of the fcc crystal grain of 40-60 μ m 2Particle dispersion, η ' precipitate mutually and the room temperature yield strength is that about 410MPa is to about 540MPa.
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