CN1271230C - Ultrahigh-strength high toughness aluminium alloy material and preparing method - Google Patents
Ultrahigh-strength high toughness aluminium alloy material and preparing method Download PDFInfo
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- CN1271230C CN1271230C CN 03119605 CN03119605A CN1271230C CN 1271230 C CN1271230 C CN 1271230C CN 03119605 CN03119605 CN 03119605 CN 03119605 A CN03119605 A CN 03119605A CN 1271230 C CN1271230 C CN 1271230C
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Abstract
The present invention discloses ultrahigh-strength and high-tenacity aluminium alloy materials and a preparing method thereof. The aluminium alloy materials comprise the alloying components: 10 to 11 wt% of Zn, 2.7 to 3.0 wt% of Mg, 1.7 to 2.0 wt% of Cu, 0.1 to 0.2 wt% of Zr, 0.1 to 0.2 wt% of Ni, and Al as the rest. According to the proportion of the alloying components, the raw materials are melted and cast into pre-preparing alloy ingots. The pre-preparing alloy ingots are melted at 800 DEG C, inert gas is used as atomizing gas, the melted alloy ingots are quickly solidified, sprayed and formed to complete the preparation of the aluminium alloy materials, and the atomizing pressure is from 0.5 to 1.0MPa. The ultrahigh-strength and high-tenacity aluminium alloy materials of the present invention has uniform alloying component, uniform microscopic structure, fine structure and no aliquation. The materials are machined in a deformation mode through hot extrusion or hot press forging; after the materials are reasonably processed in a hot mode, the ultimate tensile strength of the materials can reach more than 800Mpa; simultaneously, the elongation of the materials can be maintained at 8 to 11%. The materials can be applied to important structural parts of the fields of aerospace, nuclear industry, communication and transportation, military industry, etc.
Description
Technical field
Originally relate to invention and a kind of aluminium alloy, particularly intensity high-strength/tenacity aluminum alloy material more than 800MPa and preparation method thereof.
Background technology
Aluminium alloy has low, the easy processing of proportion, low cost and other advantages as most typical light material in the metallic substance, is a kind of dual-use material of key always.
Al-Zn-Mg-Cu (7XXX) is that alloy is the typical case's representative in the high-strength/tenacity aluminum alloy, and this alloy series is that be a class high-strength/tenacity aluminum alloy material that background develop and grow up with aerospace material in the world the sixties in 20th century.Since the seventies, industrially developed country by continue to optimize design of alloy, change the interpolation kind of various trace elements in 7000 line aluminium alloys and content, the novel thermal process technology of exploitation alloy etc., on the basis of several 7000 line aluminium alloys of primary, multiple 7000 line aluminium alloys have further been developed with better use properties, comprise 7075,7175,7475 etc., be widely used in the manufacturing of high-strength structure part in fuselage, wing shell, spar, cabin wallboard, aircraft and the rocket of various aircrafts.In the process of the various 7000 line aluminium alloy product innovations of exploitation, the researcher of countries in the world is all found: by improving the content of Zn element in 7000 line aluminium alloys, can improve the over-all properties of alloy effectively, under this thought guidance, industrially developed country has developed 7000 line aluminium alloys with higher Zn content such as 7049,7050,7076,7178 in succession, and, make the ultimate tensile strength (σ of 7000 line aluminium alloys in conjunction with the improvement of continuing to optimize to conventional cast and deformation processing, subsequent heat treatment technology
b) scope is increased to 630～680MPa from 500 early stage～580MPa, plasticity, fracture toughness property and the corrosion resistance nature of material also are improved simultaneously.But because along with the Zn content in 7000 line aluminium alloys increases, hot cracking tendency in macrosegregation in the material and the ingot casting process strengthens, the final use properties of lumber recovery when badly influencing ingot casting and material, therefore when adopting conventional cast and deformation processing technique to produce 7000 line aluminium alloys, containing the Zn amount and generally can not surpass 8 weight % in the material.Till the end of the seventies, owing to, cause the ultimate tensile strength (σ of this class alloy in the world not having breakthrough aspect preparation, shaping and the Study on Processing Technology exploitation of 7000 line aluminium alloys
b) very difficult this high point of 700MPa of breaking through.
At the nineties initial stage,, make that the strong 7000 line aluminium alloy materials of superelevation and the product of the various practicability of preparation have become reality on industrial scale along with rapid solidification/powder metallurgical technique of new generation especially spray forming technology trend is extensive practical.Aspect 7000 line aluminium alloys, with the U.S., Japan, Britain, Germany, France, Italy is that the industrially developed country of representative all adopts flash set technology to succeed in developing to contain Zn to measure strong 7000 line aluminium alloy products of superelevation of new generation more than the 8 weight % in the early 1990s, and be used to make component in structure unit, bullet train hook, racing car and other sports equipment in the various aerospacecrafts etc., established the critical role of strong 7000 line aluminium alloys of superelevation of new generation in the light-weight high-strength material evolution.
But industrially developed country still takes the form of KnowHow to be protected to a complete set of technology that reaction-injection moulding prepares the strong 7XXX line aluminium alloy of superelevation material at present at present, does not form any patent so far yet.
Summary of the invention
The purpose of this invention is to provide the ultrahigh-intensity high-toughness aluminum alloy materials of a kind of ultimate tensile strength more than 800MPa, this novel alloy improves more than 30% than traditional high-strength/tenacity aluminum alloy intensity.
Another object of the present invention provides a kind of preparation method who is applicable to the ultrahigh-intensity high-toughness aluminum alloy materials of manufacturing limit tensile strength more than 800MPa.
For achieving the above object, the present invention takes following technical scheme:
The ultrahigh-intensity high-toughness aluminum alloy materials of ultimate tensile strength of the present invention more than 800MPa by weight percentage, this alloying constituent is Zn 10～11%, Mg 2.7～3.0%, Cu1.7～2.0%, Zr 0.1～0.2%, and Ni 0.1～0.2%, all the other are Al, this material microstructure is even, and crystal grain is tiny, does not have tangible microcosmic and macrosegregation phenomenon and takes place.By appropriate heat treatment, the main mechanical property of material reaches: σ
b=800～820Mpa, σ
0.2=790～805MPa, δ
5=8～11%.
A kind of preparation method who is applicable to the ultrahigh-intensity high-toughness aluminum alloy materials of manufacturing limit tensile strength more than 800MPa of the present invention, this method comprises the steps:
(1) by alloying constituent, by weight percentage, this alloying constituent is Zn 10～11%, Mg2.7～3.0%, and Cu1.7～2.0%, Zr 0.1～0.2%, and Ni 0.1～0.2%, and all the other are Al, prepare burden preparation prealloy ingot;
(2) heat up the prefabricated ingot fusing of alloy, described is that ℃ melt alloy pig induction heating to 800～850 under insulating covering agent protection with the prefabricated ingot melting process of alloy, with the prefabricated ingot melting process of alloy is that the prefabricated ingot of alloy is melted in induction melting furnace, the temperature of induction melting furnace is controlled to be 950～1050 ℃, through the tundish heating of induction heating or resistive heating, the temperature of the tundish of induction heating or resistive heating is controlled to be 950～1050 ℃ again; The process of described atomizing is with the thrust-augmenting nozzle of melt by cooperating with unrestricted formula airflow atomizing nozzle separate type after the fusing, thrust-augmenting nozzle is induction heating or resistive heating, the temperature of thrust-augmenting nozzle is controlled to be 950～1050 ℃, afterwards, adopt argon gas or nitrogen and atomize by atomizing nozzle, atomizing nozzle is with the frequency high-speed sweep of 1～5HZ, and atomizing gas is argon gas or nitrogen, and atomizing pressure is 0.5～1.0Mpa;
(3) in aerosolization, receiving trap is high speed rotating under the traction of variable-frequency motor, and with 30～40 ° angle and the velocity pull-down of 20～40mm/min, makes billet;
(4) billet is stripped off the skin, hot extrusion or forge hot compressive strain processing, be processed into required parts;
(5) these parts are heat-treated, promptly obtain the ultrahigh-intensity high-toughness aluminum alloy materials.
Zn of the present invention, Al, Cu, Mg, Zr, Ni choose technical pure Zn, industrial pure Al, electrolysis Cu, technical pure Mg, Al-Zr master alloy, Al-Ni master alloy.
In the step (2) of method of the present invention; described is with the prealloy ingot antivacuum reaction-injection moulding equipment of packing into the prefabricated ingot melting process of alloy; ℃ melt alloy pig induction heating to 800～850 under insulating covering agent protection; insulation 10～20min makes the alloy melt homogenizing, and adds deslagging agent and refining agent carries out the degasification deslagging refining.Employed insulating covering agent is conventional insulating covering agent.Employed antivacuum reaction-injection moulding equipment is open, and promptly the equipment such as tundish of induction heating smelting furnace, induction heating or resistive heating need not be airtight, is open, do not need vacuum system.
In the step (2) of method of the present invention, the described process that atomizes is to adopt unrestricted formula airflow atomizing nozzle to atomize.
In the step (2) of method of the present invention, described high purity inert gas is argon gas or nitrogen.
In the step (3) of method of the present invention, the described process of making billet is to be undertaken by the scanning of control atomizing nozzle, the shape and the mode of motion of receiving system, and (Φ 200～300 * 300～1000mm) can to prepare the billet with typical rapid solidification tissue.
In the step (4) of method of the present invention, the described process that billet is stripped off the skin is to adopt flaying machine processing to strip off the skin, and can be prepared into the excellent base of certain specification.And under 360～420 ℃, be incubated 2 hours, carry out the process of described hot extrusion or thermal forge-pressing-forming again.
In the step (5) of method of the present invention, the described process that parts are heat-treated is to carry out the twin-stage solution treatment, makes once and the abundant Hui Rong of secondary precipitated phase, carries out T6 peak ageing treatment again.
The key of this invention is design of alloy, requires each constituent content accurate, the alloying level height, and main alloying element content height emphasizes that micro alloying element is assisted and strengthened, realizes many strengthening phases coupling and intensifying.
Another key factor of this invention is the reaction-injection moulding technology of preparing under this novel alloy condition, and the major technique details comprises following content:
Accurate for guaranteeing alloying constituent, select alap smelting temperature for use, in fusion process, add the insulating covering agent protection simultaneously, degasification slagging-off before the cast.
Select complete unrestricted formula aerosolization nozzle in the reaction-injection moulding process for use, what adopt between thrust-augmenting nozzle and the nozzle in the course of the work is to separate fit system, so that realize the nozzle high frequency sweep.For guaranteeing higher speed of cooling, atomizing pressure is selected 0.5～1.0MPa for use.Atomizing pressure is little, and speed of cooling is low, and material microstructure is thick, and grain boundary precipitate is many, atomizing pressure is big, the speed of cooling height, and material microstructure is tiny, and grain boundary precipitate is few, but material density is low, and casting yield is low, therefore selects moderate atomizing pressure in specific implementation process for use.In the patent No. 98201214.4 " double-deck unrestricted formula airflow atomizing nozzle " patent documentations by name, put down in writing the technology contents of relevant unrestricted formula airflow atomizing nozzle, the thrust-augmenting nozzle in the unrestricted formula atomizing nozzle is to take to separate fit system with the air-flow atomizing nozzle.Unrestricted formula atomizing nozzle is installed together with the injection tilting mechanism when using.Spraying tilting mechanism is to be made of nozzle oscillation cam, nozzle oscillation push rod, rotation axis, during work, driving mechanism drives the nozzle oscillation cam, the nozzle oscillation cam cooperates the airflow atomizing nozzle that drives in the unrestricted formula atomizing nozzle by rotation axis to scan swing by predefined pendulum angle and hunting frequency with the nozzle oscillation push rod, form atomizing cone, make the metal deposition moulding.This unrestricted formula airflow atomizing nozzle is a kind of known equipment.This patent has increased the substreams nozzle again and has formed double-deck unrestricted formula airflow atomizing nozzle on the basis of above-mentioned unrestricted formula airflow atomizing nozzle.The major advantage of the unrestricted formula airflow atomizing of this bilayer nozzle is: eliminated the backwash phenomenon in the metal deposition moulding process, prolonged the work-ing life of airflow atomizing spray.The unrestricted formula aerosolization nozzle of selecting for use in the reaction-injection moulding process can be above-mentioned known unrestricted formula airflow atomizing nozzle, also can be above-mentioned double-deck unrestricted formula airflow atomizing nozzle.
Be to guarantee carrying out continuously of preparation process, the present invention has studied a kind of highly purified SiN pottery thrust-augmenting nozzle material, and this material can anti-high temperature more than 1000 ℃, and has good erosion resistibility and the heat resistanceheat resistant performance of shaking.
Receiving trap is made up of take-up reel, back shaft, rotation traction traction motor, lifting traction electric machine, transmission rig, dynamic seal system, take-up reel under the traction of rotation traction traction motor and lifting traction electric machine, can realize high speed rotating (0～120rpm) and stepless change descend (0～30mm/s).In preparation process, metal melt stream is broken into a large amount of tiny drops by the atomizing gas of high-speed flight, under the effect of gravity and atomizing gas, be accelerated flight forward, before solidifying but also do not solidify fully, atomizing droplet deposits in the take-up reel, by the speed of rotation and the lowering speed of control take-up reel, can obtain the billet of certain diameter.
In the step (4) of method of the present invention, the process of described described hot extrusion, its extrusion temperature is 360 ℃～420 ℃, be incubated 1.5h, and extrusion speed is 1～5m/min, and extrusion ratio reaches as high as 40: 1.
In the step (5) of method of the present invention, described with parts heat-treat comprise solution treatment and aging treatment process, the main purpose of solution treatment be make that the reaction-injection moulding preparation and the thermal distortion course of processing separate out once with the abundant Hui Rong of secondary precipitated phase.
Solution treatment can be the single-stage solid solution among the present invention, and solid solubility temperature is 485～490 ℃/3h, also can be the twin-stage solid solution, and solid solubility temperature is 435～440 ℃/5h+485～490 ℃/1h.Aging temp can adopt 120 ℃/24h of single-stage aging, also can adopt 120 ℃ of two-stage time effects/24h+180 ℃/60min.Ultimate tensile strength through material after the ageing treatment can reach more than the 800MPa.
Advantage of the present invention is:
(1) the material alloys composition is accurate, and microstructure is evenly tiny, no significant defect and macrosegregation;
(2) this material has good thermal distortion working ability;
(3) this material is through suitable thermal treatment, and the ultimate tensile strength of material can reach more than the 800MPa, keeps higher plasticity simultaneously, is a kind of high performance structural material.
Description of drawings
Fig. 1 is an antivacuum reaction-injection moulding device structure synoptic diagram of the present invention
Fig. 2 is a receiving trap structural representation of the present invention
Fig. 3 is an alloy block material microtexture photo of the present invention
Fig. 4 is the prepared billet photo of the present invention
Embodiment
The present invention can take following antivacuum reaction-injection moulding equipment to cooperate method of the present invention to be prepared powdered alloy.As shown in Figure 1, this antivacuum reaction-injection moulding equipment is to adopt to receive tank body 2, is provided with the tundish 4 of induction heating smelting furnace (not graphic), induction heating or resistive heating outside the top of reception tank body 2 from top to bottom successively.To the outlet of induction melting furnace, and the outlet of the tundish 4 of induction heating or resistive heating connects thrust-augmenting nozzle 5 in the import of induction heating tundish 4, and thrust-augmenting nozzle 5 becomes 30～40 ° of angles with the vertical line of horizontal plane, and the outlet of thrust-augmenting nozzle 5 feeds and receives in the tank body 2.Around thrust-augmenting nozzle 5 tube walls, be provided with heating system (not graphic), and be provided with unrestricted formula airflow atomizing nozzle 7 in the exit of thrust-augmenting nozzle 5, the outlet section of thrust-augmenting nozzle 5 is positioned at the centre of unrestricted formula airflow atomizing nozzle, and what adopt between thrust-augmenting nozzle 5 and the unrestricted formula airflow atomizing nozzle 7 is to separate fit system.Because the alloy atomization temperature is very high, therefore in the aerosolization process, select complete unrestricted formula aerosolization nozzle for use, what adopt between thrust-augmenting nozzle and the nozzle in the course of the work is to separate fit system.Adopt this nozzle to carry out the preparation of aerosolization powdered alloy, the variety of problems of having been brought when having avoided high-meltiing alloy to atomize using to the restraint-type nozzle.Because when atomizing, atomizing gas will constantly flow into (flow is determined by nozzle parameter and atomizing pressure) therefore is provided with exhaust system in the bottom that receives tank body 2 interface from atomizing nozzle, atomizing gas is discharged receive tank body 2, and require the exhaust system airshed greater than the atomizing gas flow.
The receiving trap of preparation billet is installed in receiving tank body 2, and this receiving trap is a known equipment.As shown in Figure 3, receiving trap comprises two portions, be rotating part 21 and lifting unit 22, rotating part 21 be on received block 23, be provided with rotation traction traction motor 24, this rotation traction traction motor 24 is connected with back shaft 26 power by transmission rig, this back shaft 26 is provided with take-up reel 27; Lifting unit 22 is to be provided with lifting traction electric machine 28 on support, this lifting motor is connected with leading screw 30 power by transmission rig 29, and on support, be provided with the feed rod 31 parallel with leading screw 30, received block 23 affixed stroke spares 32, stroke spare 32 is provided with nut and casinghead, nut and leading screw 30 are spirally connected, casinghead and feed rod 31 sockets, in preparation process, start rotation traction traction motor 24, high speed rotating take-up reel 23, and start lifting traction electric machine 28, leading screw 30 is rotated, nut also moves thereupon, and is that track slides on feed rod 31 with feed rod 31, with certain angle and velocity pull-down take-up reel 27, atomizing droplet is directly deposited in the take-up reel 27, obtain the billet of certain diameter.
Above-mentioned preparation facilities is in order to cooperate processing method of the present invention, to be not limited to this preparation facilities but finish method of the present invention, also can adopting the preparation facilities of alternate manner to carry out processing method of the present invention.
Embodiment 1:
After the prefabricated ingot of alloyage, the smelting furnace of packing into is warming up to 850 ℃, insulation 10min, and the reaction-injection moulding preparation is carried out in the slagging-off degasification, adopts high-purity argon gas to carry out atomizing pressure 1.0Mpa.As shown in Figure 2, opening rotating machine 24, lifting motor 28, is 60～120rpm with rotating speed, high speed rotating take-up reel, thrust-augmenting nozzle 5 become 35 ° of angles with the vertical line of horizontal plane, drop-down speed is 20～30mm/min, drop-down take-up reel 27 directly deposits in the take-up reel 27 atomizing droplet.150 kilograms of novel alloys of disposable continuous atomizing, alloying constituent is: Zn 10 weight %, Mg 2.7 weight %, Cu1.7%, Zr 0.1%, and Ni 0.1%, all the other are Al, prepare the novel high-strength/tenacity aluminum alloy billet of heavy 100Kg, and prepared billet photo as shown in Figure 4.This deposition blank is processed into the excellent base of certain specification, at 420 ℃ of insulation 2h, carry out hot extrusion processing with 25: 1 extrusion ratios, squeeze out the pole of φ 40mm, 435～440 ℃/5h+485～490 ℃/1h solution treatment, institution of prescription can adopt 120 ℃/24h of single-stage aging, and ultimate tensile strength is 810MPa, and unit elongation is 10% simultaneously.As shown in Figure 3, this material microstructure is tiny, no significant defect and macrosegregation.
Embodiment 2:
After the prefabricated ingot of alloyage, the smelting furnace of packing into is warming up to 800 ℃, insulation 10min, the slagging-off degasification, carry out the reaction-injection moulding preparation, adopt high-purity argon gas to carry out atomizing pressure 0.8MPa, 100 kilograms of novel alloys of disposable continuous atomizing, alloying constituent is: Zn 11 weight %, Mg 3.0 weight %, Cu2.0%, Zr 0.2%, Ni 0.2%, and all the other are Al, prepares the novel high-strength/tenacity aluminum alloy billet of heavy 70Kg, this deposition blank is processed into the excellent base of certain specification, at 360 ℃ of insulation 2h, carry out hot extrusion processing with 39: 1 extrusion ratios, squeeze out the pole of Φ 25mm, 435～440 ℃/5h+485～490 ℃/1h solution treatment, institution of prescription can adopt 120 ℃/24h of single-stage aging, and ultimate tensile strength is 820MPa, and unit elongation is 8% simultaneously.
Claims (4)
1, a kind of ultrahigh-intensity high-toughness aluminum alloy materials is characterized in that: by weight percentage, this alloying constituent is Zn10～11%, Mg2.7～3.0%, and Cu1.7～2.0%, Zr0.1～0.2%, Ni0.1～0.2%, all the other are Al.
2, a kind of method for preparing the ultrahigh-intensity high-toughness aluminum alloy materials, it is characterized in that: this method comprises the steps:
(1) by alloying constituent, by weight percentage, this alloying constituent is Zn10～11%, Mg2.7～3.0%, and Cu1.7～2.0%, Zr0.1～0.2%, Ni0.1～0.2%, all the other are Al, prepare burden preparation prealloy ingot;
(2) heat up the prefabricated ingot fusing of alloy, described is that ℃ melt alloy pig induction heating to 800～850 under insulating covering agent protection with the prefabricated ingot melting process of alloy, with the prefabricated ingot melting process of alloy is that the prefabricated ingot of alloy is melted in induction melting furnace, the temperature of induction melting furnace is controlled to be 950～1050 ℃, through the tundish heating of induction heating or resistive heating, the temperature of the tundish of induction heating or resistive heating is controlled to be 950～1050 ℃ again; The process of described atomizing is with the thrust-augmenting nozzle of melt by cooperating with unrestricted formula airflow atomizing nozzle separate type after the fusing, thrust-augmenting nozzle is induction heating or resistive heating, the temperature of thrust-augmenting nozzle is controlled to be 950～1050 ℃, afterwards, adopt argon gas or nitrogen and atomize by atomizing nozzle, atomizing nozzle is with the frequency high-speed sweep of 1～5HZ, and atomizing gas is argon gas or nitrogen, and atomizing pressure is 0.5～1.0Mpa;
(3) in aerosolization, receiving trap is high speed rotating under the traction of variable-frequency motor, and with 30～40 ° angle and the velocity pull-down of 20～40mm/min, makes billet;
(4) billet is stripped off the skin, hot extrusion or forge hot compressive strain processing, be processed into required parts;
(5) these parts are heat-treated, promptly obtain the ultrahigh-intensity high-toughness aluminum alloy materials.
3, the method for preparing the ultrahigh-intensity high-toughness aluminum alloy materials according to claim 2, it is characterized in that: in the described step (4), the described process that billet is stripped off the skin is to adopt flaying machine processing to strip off the skin, be prepared into the excellent base of certain specification, and under 360～420 ℃, be incubated 2 hours, carry out the process of described hot extrusion or thermal forge-pressing-forming again.
4, according to claim 2 or the 3 described methods that prepare the ultrahigh-intensity high-toughness aluminum alloy materials, it is characterized in that: in the described step (5), the described process that parts are heat-treated is to carry out the twin-stage solution treatment, make once and the abundant Hui Rong of secondary precipitated phase, carry out T6 peak ageing treatment again.
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| CN 03119605 CN1271230C (en) | 2003-03-14 | 2003-03-14 | Ultrahigh-strength high toughness aluminium alloy material and preparing method |
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| CN1271230C true CN1271230C (en) | 2006-08-23 |
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| CN101415855B (en) * | 2006-04-13 | 2011-12-28 | 空中客车德国有限公司 | Method and apparatus for thermally processing sectional materials, and sectional materials |
| JP5059512B2 (en) * | 2007-02-28 | 2012-10-24 | 株式会社神戸製鋼所 | High strength, high ductility Al alloy and method for producing the same |
| CN102002615B (en) * | 2010-10-21 | 2012-11-21 | 哈尔滨工业大学 | Ultrahigh-strength aluminum alloy material and preparation method of pipe blank for preparing internal cylinder of separator |
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| KR101760076B1 (en) * | 2016-06-09 | 2017-07-24 | 한국기계연구원 | Al-Zn alloy comprising precipitation with improved strength and elongation and method of manufacturing the same |
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| CN109266879A (en) * | 2018-11-20 | 2019-01-25 | 天津百恩威新材料科技有限公司 | A kind of Bradley bistrique and high-strength aluminum alloy are preparing the application in Bradley bistrique |
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2003
- 2003-03-14 CN CN 03119605 patent/CN1271230C/en not_active Expired - Lifetime
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