CN107739865A - A kind of high intensity, high-modulus in-situ Al-base composition and preparation method thereof - Google Patents

Abstract

The present invention relates to aluminum matrix composite, specifically a kind of high intensity, high-modulus in-situ Al-base composition and preparation method thereof.The aluminum matrix composite is regulated and controled using commercial-purity aluminium as raw material by composition, and micro-/ nano Composite, alloying, deformation processing and heat treatment technics in situ are combined, and collaboration improves the intensity and modulus of alloy.Under electromagnetic field regulation and control, the reinforced particle size for reacting generation is micro/nano level, is evenly distributed, reinforcement fabricated in situ yield height, is readily synthesized the high high intensity of reinforcement content, high-modulus aluminum based composite material enhanced by granules in situ.

Description

A kind of high-strength, high-modulus in-situ aluminum matrix composite material and its preparation method

technical field

The invention relates to an aluminum-based composite material, in particular to a high-strength, high-modulus in-situ aluminum-based composite material and a preparation method thereof.

Background technique

The raw material resources required for the preparation of particle reinforcement in particle reinforced aluminum matrix composites are abundant, the preparation process is simple, the design is strong, and it has excellent comprehensive mechanical properties and performance, such as high specific strength, high specific modulus, high specific Stiffness, low density, low thermal expansion coefficient, etc., so it is mainly used in aerospace, ocean engineering, automobile industry and other fields. It is worth noting that an important reason that restricts the wide application of particle reinforced aluminum matrix composites is that the elastic modulus cannot meet the application requirements. As a structural material, the elastic modulus is generally required to reach 80GPa, and some requirements are even higher. It can be seen that on the basis of satisfying other mechanical properties of composite materials, it is very necessary to develop high elastic modulus particle-reinforced aluminum matrix composites to meet application requirements. The preparation technology of particle reinforced aluminum matrix composites can be roughly divided into solid state synthesis technology, liquid state synthesis technology and other synthesis technologies.

As a new breakthrough composite technology, the in-situ reaction synthesis technology has been widely valued by scholars at home and abroad. One of the most effective ways to industrialize aluminum matrix composites. The unique feature of the in-situ reaction preparation technology to synthesize particle-reinforced aluminum matrix composites is that the reinforced particles are formed in situ from the aluminum matrix by in-situ nucleation and growth through chemical reactions between components during the preparation process. Compared with the traditional aluminum matrix composites with external particles, the advantages of in-situ synthesized particle-reinforced aluminum matrix composites are as follows: (1) The in-situ self-generated reinforced particle phase is thermodynamically stable in the matrix, especially when the aluminum matrix composites are in When applied at a higher temperature, the reinforced particle phase will not decompose or transform into other phases, so the macroscopic physical and chemical properties of the composite material can be guaranteed. (2) The interface between the particle-reinforced phase synthesized in situ and the Al matrix is clean and interatomic, and the interface strength is high. (3) The in-situ synthesized particle-reinforced phase can be finer than the external particle size, and it is easy to disperse in the aluminum matrix grains, so that the elastic modulus, yield strength and friction and wear properties of the in-situ aluminum matrix composite are significantly improved. improve. However, there are still two major problems to be solved in the development of particle reinforced aluminum matrix composites: (1) With the development of high-end fields such as aerospace and marine engineering, higher requirements are put forward for the strength and modulus of materials in key parts. Traditional materials can no longer meet this requirement; (2) Poor wettability between reinforcing particles and the matrix leads to high residual stress of the material, and high residual stress composite components are severely deformed or even cracked and scrapped in the subsequent machining process; in order to avoid machining During the process, residual stress causes component cracking, and the machining process of high residual stress components is strictly limited, which will reduce the production efficiency of components and increase production costs.

The investigation of the existing technical literature and review literature shows that at present, the strength of the material is further improved and the residual stress of the material is reduced mainly through the alloying of a large number of rare earth elements, the composite strengthening of particles, and the harsh heat treatment process (such as: patent CN102127665A, CN103627932A , CN103628007A). However, the above-mentioned harsh process technology still has the following shortcomings and deficiencies: (1) the use of a large number of expensive rare earth elements, such as Sc, Gd, etc., greatly increases the manufacturing cost of the material, and the mechanical properties are not significantly improved, and The modulus of the material cannot be effectively improved, so the stiffness of the material cannot be fundamentally improved and the residual stress of the material cannot be reduced. (2) Large-sized reinforcing particles are conducive to improving the strength of the material and have good dispersibility, but it is difficult to wet the matrix and have many defects. In addition, from the analysis of the current reinforcement mechanism, in the case of the same particle volume fraction, the smaller the size, the stronger the reinforcement effect. However, the reduction of the particle size increases the specific surface energy of the particles. Energies tend to come together. (3) The elimination of material stress by heat treatment is often accompanied by the sacrifice of strength, and the reduction is not large.

Contents of the invention

The purpose of the present invention is to provide a high-strength, high-modulus in-situ aluminum-based composite material, which has high strength, high modulus and low stress.

Another object of the present invention is to provide a method for preparing high-strength, high-modulus in-situ aluminum-matrix composites, using in-situ reaction technology to prepare binary ceramic particle-reinforced micro/nano-aluminum-matrix composites to achieve raw material strength and mold The amount of significantly improved, while having a lower residual stress.

The technical scheme adopted by the present invention in order to achieve its technical purpose is to prepare particle reinforced aluminum matrix composites by melt direct reaction method through Al-K ₂ TiF ₆ -K ₂ ZrF ₆ -KBF ₄ reaction system, and add microalloying elements Further improve material performance. Deformation processing is carried out on the prepared composite material, and finally solid solution strengthening is carried out through heat treatment, so as to finally obtain the high-strength, high-modulus in-situ aluminum-based composite material of the present invention.

Compared with the existing preparation technology, the characteristics of this technical solution are mainly reflected in the successful introduction of binary ceramic micro/nano reinforcement particles into the Al-Zn-Mg-Cu ultra-high strength aluminum alloy through the in-situ endogenous method, and at the same time , through the addition of rare earths Y and Er to synergistically regulate the strength and plasticity of Al matrix composites. This technology adopts the in-situ aluminum-based composite material prepared by the magnetochemical in-situ reaction method, which solves the shortcomings of low modulus of Al-Zn-Mg-Cu ultra-high-strength aluminum alloy, poor wettability and high internal stress of the composite material prepared by the external method. . Therefore, the composite material prepared by this technology can be widely used in high-end fields such as aerospace and marine engineering.

Realize the concrete steps of the present invention as follows:

(1) Preparation of fluoride salt: Dry the fluoride salt required for the reaction in a drying oven to remove crystal water, grind it after cooling in the furnace, weigh it in proportion, and wrap it with aluminum foil for use.

(2) In-situ micro/nano particle strengthening: Melting pure aluminum in an intermediate frequency crucible induction furnace, after the temperature rises to the reaction temperature, put the fluorine salt prepared in step (1) into the crucible, and use The graphite rod is stirred evenly, and then reacted under the action of an electromagnetic field for a certain period of time to obtain micro/nano TiB ₂ and ZrB ₂ particles in the matrix, and the obtained composite material melt is refined, deslagged, and degassed to obtain a composite material melt And keep it aside.

(3) Alloying: Alloying the composite material obtained in step (2). That is to add pure Zn, pure Cu, Al-Zr, Al-Mn, Al-Er and Al-Y master alloys to the melt in turn, react for a certain period of time under the action of an electromagnetic field, and then refine and remove slag from the melt again , Degassing. Then add pure Mg into the melt, react at a certain temperature for a certain period of time, and then cast it in a preheated copper mold after the temperature drops to a certain level.

(4) Homogenization treatment: after cooling the ingot of the composite material obtained in step (3), homogenization treatment is performed to eliminate structure segregation.

(5) Deformation processing: In order to further improve the strength of the composite material, the composite material obtained in step (4) is subjected to deformation processing.

(6) Heat treatment: performing heat treatment on the composite material obtained after the deformation processing in step (4), to precipitate the strengthening phase and realize the strengthening of the composite material.

The fluorine salts described in step (1) are K ₂ TiF ₆ , K ₂ ZrF ₆ and KBF ₄ , the drying temperature is 200-300°C, and the drying time is 90-180 min. The reaction mixed salt should be of industrial pure grade, ground on a ball mill to obtain a fine powder below 200 mesh, and then weigh K ₂ TiF according to the mass ratio K ₂ TiF ₆ :K ₂ ZrF ₆ :KBF ₄ :=43:42:126 ₆ ,

K ₂ ZrF ₆ , KBF ₄ reaction salt, wherein KBF ₄ is in excess of 50%. The addition amount of K ₂ TiF ₆ , K ₂ ZrF ₆ and KBF ₄ is 10%-50% of the mass of the aluminum alloy.

In the step (2), the reaction temperature of the fluorine salt and the aluminum melt is 840-880° C., and the reaction time is 20-60 minutes. Control the excitation current to 170-220A, the electromagnetic stirring frequency to 5-15Hz, and the electromagnetic stirring time to 10-20min. The purpose of the refining, deslagging and degassing treatment is to remove residual slag, impurities and gas in the composite melt. The standing temperature is 750-800° C., and the standing time is 1-2 minutes.

Among them, the reaction formula of K ₂ TiF ₆ , K ₂ ZrF ₆ and KBF ₄ with the melt is:

3K ₂ TiF ₆ +3K ₂ ZrF ₆ +12KBF ₄ +20Al＝3TiB ₂ +3ZrB ₂ +18KAlF ₄ +2K ₃ AlF ₆ ;

Among them, KAlF ₄ and K ₃ AlF ₆ have poor wettability with aluminum and need to be removed during the slag removal in step (2).

The alloying described in step (3), after adjustment, the mass percentage content of elements in the composite material melt is respectively Zn:8.0-10.0, Cu:1.2-2.6, Mg:1.8-2.8, Y:0.1-0.3, Er: 0.1-0.3, ZrB ₂ : 0-10, TiB ₂ : 0-10, Si≤0.10, Fe≤0.15, Mn≤0.05, Cr≤0.04, and the rest are Al. After adding pure Zn, pure Cu, Al-Zr, Al-Mn, Al-Er and Al-Y master alloy, the reaction temperature is 720-780°C, the reaction time is 5-10min, the electromagnetic stirring time is 3-5min, stirring When controlling the excitation current to 170-220A, the electromagnetic stirring frequency is 5-15Hz. The purpose of the refining, deslagging and degassing treatment is to remove residual slag, impurities and gas in the melt. The reaction temperature after adding pure Mg is 680-700° C., and the reaction time is 3-5 minutes. The preheating temperature of the copper mold is 200-250°C, and the final pouring temperature is 720±10°C.

The homogenization treatment parameters described in the step (4) are: heating from room temperature to 440-460°C within 1-2 hours, keeping the temperature for 12-24 hours, and then cooling to room temperature with the furnace.

The deformation processing method described in step (5) is one or more of extrusion, forging, and rolling processes. The characteristic parameters are controlled as ①: extrusion: extrusion temperature is 420-440°C, extrusion ratio is 20:1-5:1, extrusion speed is 5-10mm/s; ②: forging: forging temperature is 400-450 ℃, the amount of deformation is 50%-70%; ③: Rolling: the rolling temperature is 420-440°C, the rolling speed is 5-15mm/s, the amount of each pressing is 0.5-2mm, and the total deformation rate is 50 -80%.

The heat treatment regime described in step (6) includes solid solution and aging treatment. The solution treatment system is to rise from room temperature to 450-460°C within 1-2 hours, keep it warm for 2-3 hours, then rise to 470-480°C within 0.5-1 hour, keep it warm for 2 hours, and then put it in a water bath at 30-60°C Medium quenching treatment, the quenching transfer time is less than 8 seconds; the aging treatment system is to rise from room temperature to 115-120°C, keep warm for 18-24 hours and then cool with the furnace.

The present invention has following advantage and effect:

①Under the action of the electromagnetic field, the size of the particles produced by the reaction is micro/nano scale, the agglomeration phenomenon is obviously improved, and the yield of the composite material is high, which is conducive to improving the mechanical properties of the prepared composite material.

② The required raw materials come from a wide range of sources and low cost, which is conducive to the realization of large-scale production, has excellent economic and social benefits, and has a good application prospect.

③ Compared with the external addition method, the wettability between the reinforced particles and the matrix is significantly improved, so that the prepared composite material has lower residual stress.

Description of drawings

The accompanying drawings are used to further illustrate the present invention, but are not meant to limit the protection scope of the present invention.

Fig. 1 is the preparation process flowchart of the embodiment of the present invention.

Fig. 2 is the SEM image of the composite material prepared under the process conditions described in Example 1. It can be seen from the figure that the average particle size is 80nm, and the distribution is uniform.

Figure 3 is the EDS image of the reinforcement particles in the composite material prepared under the process conditions described in Example 1, which shows that Ti, Zr, and B are included, which proves that TiB ₂ and ZrB ₂ particles were successfully prepared.

detailed description

Below the embodiment of the present invention is described in detail, present embodiment implements under the premise of technical solution of the present invention, has provided detailed embodiment and concrete operation process, but protection scope of the present invention is not limited to following implementation example.

Example 1:

A high-strength, high-modulus in-situ aluminum matrix composite material with a volume fraction of reinforcing particles of 4vol.% was prepared, and its composition mass percentages were Zn:8.2, Mg:2.1, Cu:2.3, Mn:0.04, Y:0.2, Er : 0.2, ZrB ₂ : 3.1, TiB ₂ : 4.2, Si<0.10, Fe<0.15, Cr<0.04, and the balance is Al. The specific method is:

Dry the fluorine salts (K ₂ TiF ₆ , K ₂ ZrF ₆ , KBF ₄ ) required for the reaction to remove crystal water in a drying oven at a temperature of 250°C for 180 minutes, cool in the furnace and grind to 200 mesh Next, weigh K ₂ TiF ₆ , K ₂ ZrF ₆ , and KBF ₄ reaction salts according to the mass ratio (K ₂ TiF ₆ :K ₂ ZrF ₆ :KBF ₄ :=43:42:126), wherein KBF ₄ is in excess of 50% , mix well and wrap with aluminum foil for later use. Melt pure aluminum in an intermediate frequency crucible-type induction furnace. After the temperature rises to 850°C, put the prepared fluorine salt into the crucible in batches with pliers, stir evenly with a graphite rod, and react under the action of an electromagnetic field for 15 minutes. , where the excitation current is controlled to 200A, the electromagnetic stirring frequency is 10Hz, and then reacted for 15min without the action of a magnetic field, and the temperature is controlled at 840-880°C during the whole reaction process. Refining, deslagging and degassing are carried out on the obtained composite material melt, and then stand still for use. After the temperature drops below 780°C, add pure Zn, pure Cu, Al-Zr, Al-Mn, Al-Er and Al-Y master alloys to the melt in turn, and react under the action of an electromagnetic field for 3 minutes, in which the excitation is controlled The current is 200A, the frequency of electromagnetic stirring is 10Hz, and then react for 7 minutes without the action of magnetic field, and the temperature is controlled at 720-780°C during the whole reaction process. Refining, deslagging and degassing are performed on the obtained melt again, and then it is left standing for use. When the temperature drops below 700°C, add pure Mg, react for 5 minutes, raise the temperature to 720°C, and cast it into an ingot. After the ingot was cooled to room temperature, it was homogenized at 450°C for 24 hours. The homogenized ingot is processed into a certain rolling size. The rolling block was kept at 420° C. for 10 minutes, and then hot-rolled at a rolling speed of 10 mm/s, with a pressing force of 1 mm each time, and a total deformation rate of 68%, to finally obtain a plate with a thickness of 4 mm. The plate is subjected to two-stage solid solution at 450°C/2h+475°C/2h, followed by T6 single-stage aging treatment at 120°C/24h. The solution treatment system is to rise from room temperature to 450°C within 1 hour, hold for 2 hours, then rise to 475°C within 0.5 hour, hold for 2 hours, and then quench in a 50°C water bath, and the quenching transfer time is less than 8 seconds. The aging treatment system is to rise from room temperature to 120°C, keep warm for 24 hours and then cool with the furnace.

The mechanical performance test shows that the tensile strength of the composite material after rolling + heat treatment is 680MPa, the yield strength is 650MPa, the elongation is 6.5%, the elastic modulus is 83GPa, and the residual stress is -52MPa.

Example 2:

A high-strength, high-modulus in-situ aluminum matrix composite material with a volume fraction of reinforcing particles of 5vol.% was prepared, and its composition mass percentages were Zn 9.8, Mg 2.2, Cu 1.5, Mn 0.03, Y:0.15, Er:0.25, ZrB ₂ : 3.8, TiB ₂ : 5.1, Si<0.10, Fe<0.15, Cr<0.04, and the balance is Al. The balance is Al. The specific method is:

Dry the fluorine salts (K ₂ TiF ₆ , K ₂ ZrF ₆ , KBF ₄ ) required for the reaction to remove crystal water in a drying oven at a temperature of 250°C for 180 minutes, cool in the furnace and grind to 200 mesh Next, weigh K ₂ TiF ₆ , K ₂ ZrF ₆ , and KBF ₄ reaction salts according to the mass ratio (K ₂ TiF ₆ :K ₂ ZrF ₆ :KBF ₄ :=43:42:126), wherein KBF ₄ is in excess of 50% , mix well and wrap with aluminum foil for later use. Melt pure aluminum in an intermediate frequency crucible-type induction furnace. After the temperature rises to 850°C, put the prepared fluorine salt into the crucible in batches with pliers, stir evenly with a graphite rod, and react under the action of an electromagnetic field for 15 minutes. , where the excitation current is controlled to 200A, the electromagnetic stirring frequency is 10Hz, and then reacted for 15min without the action of a magnetic field, and the temperature is controlled at 840-880°C during the entire reaction process. Refining, deslagging and degassing are carried out on the obtained composite material melt, and then stand still for use. After the temperature drops below 780°C, add pure Zn, pure Cu, Al-Zr, Al-Mn, Al-Er and Al-Y master alloys to the melt in turn, and react under the action of an electromagnetic field for 3 minutes, in which the excitation is controlled The current is 200A, the frequency of electromagnetic stirring is 10Hz, and then react for 7 minutes without the action of magnetic field, and the temperature is controlled at 720-780°C during the whole reaction process. Refining, deslagging and degassing are performed on the obtained melt again, and then it is left standing for use. When the temperature drops below 700°C, add pure Mg, react for 5 minutes, raise the temperature to 720°C, and cast it into an ingot. After the ingot was cooled to room temperature, it was homogenized at 450°C for 24 hours. The homogenized ingot is processed into a certain extrusion size. The extrusion temperature is 430° C., the extrusion ratio is 5:1, and the extrusion speed is 5 mm/s. The obtained extruded rods were subjected to two-stage solid solution at 450°C/2h+475°C/2h, followed by T6 single-stage aging treatment at 120°C/24h. The solution treatment system is to rise from room temperature to 450°C within 1 hour, hold for 2 hours, then rise to 475°C within 0.5 hour, hold for 2 hours, and then quench in a 50°C water bath, and the quenching transfer time is less than 8 seconds. The aging treatment system is to rise from room temperature to 120°C, keep warm for 24 hours and then cool with the furnace.

The mechanical performance test shows that the tensile strength of the composite material after rolling + heat treatment is 700MPa, the yield strength is 680MPa, the elongation is 5.5%, the elastic modulus is 85GPa, and the residual stress is -45MPa.

From the above results, it can be seen that the high-strength, high-modulus in-situ aluminum-based composite material of the present invention can be stably prepared under the described preparation process with a tensile strength exceeding 680MPa, a yield strength exceeding 650MPa, and an elongation It is a high-strength, high-modulus aluminum-based composite material with a residual stress of less than 60 MPa and a relatively low cost, so it has great application potential in aerospace, transportation, and weapon industries.

Claims (7)

1. the preparation method of a kind of high intensity, high-modulus in-situ Al-base composition, it is characterised in that comprise the following steps that：

(1) preparation of villiaumite：Villiaumite needed for reacting is dried in drying box removes the crystallization water, grinds and presses after furnace cooling Ratio weighs, and is coated with aluminium foil stand-by；

(2) micro-/ nano particle strengthening in situ：Fine aluminium is subjected to melting in intermediate frequency induction crucible furnace, treats that temperature rises to reaction After temperature, the villiaumite got ready in step (1) is put into crucible, and stirred with graphite rod, then in electromagnetic field effect The lower reaction regular hour, micro-/ nano TiB is obtained in the base₂And ZrB₂Particle, essence is carried out to the Composite Melt of acquisition Refining, slagging-off, degasification, obtain Composite Melt and set aside for use；

(3) alloying：Alloying is carried out to the composite obtained by step (2).Pure Zn, pure Cu are added into melt successively, Al-Zr, Al-Mn, Al-Er and Al-Y intermediate alloy, react the regular hour under electromagnetic field effect, then melt is entered again Row refining, slagging-off, degasification；Then pure Mg is added in melt, reacted at a certain temperature certain time, then treats that temperature drops It is low to a certain extent after poured into a mould in the copper mold of preheating；

(4) Homogenization Treatments：After composite ingot casting cooling made from step (3), Homogenization Treatments are carried out, are eliminated with this Microstructure segregation；

(5) deformation processing is handled：In order to further lift composite material strength, the composite obtained to step (4) becomes Shape working process；

(6) it is heat-treated：The composite obtained after the processing of step (4) deformation processing is heat-treated, separates out hardening constituent, it is real The reinforcing of existing composite.

2. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the villiaumite described in step (1) is K₂TiF₆, K₂ZrF₆And KBF₄, drying temperature is 200-300 DEG C, time 90- 180min.Reaction salt-mixture should use technical pure rank, on ball mill grind obtain the fine powder below 200 mesh, then according to Mass ratio K₂TiF₆:K₂ZrF₆:KBF₄:=43:42:126, weigh K₂TiF₆, K₂ZrF₆, KBF₄Reacting salt, wherein KBF₄It is excessive 50%.K₂TiF₆, K₂ZrF₆And KBF₄Addition be aluminium alloy quality 10%-50%.

3. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the reaction temperature of villiaumite and aluminum melt is 840-880 DEG C, reaction time 20-60min in step (2), controls exciting current 170-220A, electromagnetic agitation frequency are 5-15Hz, and the electromagnetic agitation time is 10-20min；At described refining, slagging-off and degasification Reason, it is therefore an objective to remove the slag remained in compounding flux, impurity and gas, described dwell temperature is 750-800 DEG C, standing Time is 1-2min.

4. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the alloying described in step (3), the mass percentage content that element in Composite Melt is made after adjustment is respectively Zn: 8.0-10.0, Cu:1.2-2.6, Mg:1.8-2.8, Y:0.1-0.3, Er:0.1-0.3, ZrB₂:0-10, TiB₂:0-10,Si≤ 0.10, Fe≤0.15, Mn≤0.05, Cr≤0.04, remaining is Al；Add pure Zn, pure Cu, Al-Zr, Al-Mn, Al-Er and Al- Reaction temperature after Y intermediate alloys is 720-780 DEG C, reaction time 5-10min, and the electromagnetic agitation time is 3-5min, stirring When control exciting current 170-220A, electromagnetic agitation frequency is 5-15Hz；Described refining, slagging-off and degassing processing, it is therefore an objective to Remove slag, impurity and the gas remained in melt；The reaction temperature added after pure Mg is 680-700 DEG C, reaction time 3- 5min.Copper mold preheating temperature is 200-250 DEG C, and last pouring temperature is 10 DEG C of 720 scholar.

5. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the Homogenization Treatments parameter described in step (4) is：440-460 DEG C is warming up within 1-2 hours from room temperature, is incubated 12-24 Hour, then cool to room temperature with the furnace.

6. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the deformation processing processing mode described in step (5) is extruding, forged, the one or more in rolling mill practice.Characteristic parameter Control as 1.：Extruding：Extrusion temperature is 420-440 DEG C, extrusion ratio 20:1-5:1, extrusion speed 5-10mm/s；②：Forging Make：Forging temperature is 400-450 DEG C, deflection 50%-70%；③：Rolling：Rolling temperature is 420-440 DEG C, mill speed For 5-15mm/s, each volume under pressure is 0.5-2mm, total deformation rate 50-80%.

7. a kind of high intensity, the preparation method of high-modulus in-situ Al-base composition as claimed in claim 1, its feature exist In the heat treating regime described in step (6) includes solid solution and Ageing Treatment；Solution treatment system is within room temperature 1-2 hours 450-460 DEG C is risen to, is incubated 2-3 hours, 470-480 DEG C is then risen within 0.5-1 hours, 2 hours are incubated, then in 30- Quenching Treatment in 60 DEG C of water-baths, quenching shift time are less than 8 seconds；System of ageing treatment is to rise to 115-120 DEG C from room temperature, insulation Furnace cooling after 18-24 hours.