CN103589977A - Method for improving the fatigue resistance performance of Al-Cu-Mg alloy - Google Patents
Method for improving the fatigue resistance performance of Al-Cu-Mg alloy Download PDFInfo
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Abstract
A method for improving the fatigue resistance performance of Al-Cu-Mg alloy is to perform high-temperature hot rolling, primary solution treatment, large deformation cold rolling, secondary solution treatment and natural aging treatment to homogenized aluminium alloy in sequence. According to the invention, relatively high temperature is kept before hot rolling, and then a material recrystallizes dynamically during the hot rolling process, so that a plurality of recrystallization textures such as Goss and Cube are formed, and the fatigue resistance performance of the aluminium alloy can be improved advantageously; solution treatment before cold rolling can greatly eliminate large second-phase particles except for impurities such as Fe and Si to prevent a high energy region from forming, so that uneven recrystallization can be avoided; after large deformation cold rolling deformation is performed, the dislocation density of the alloy is greatly improved, the alloy can obtain more stored energy, the recrystallization nucleation rate is increased during solution treatment, fine crystal grains can be formed, and the fatigue resistance performance of the aluminium alloy can be improved further. The process method provided by the invention is simple, convenient in operation, economical in cost and suitable for industrialized application.
Description
Technical field
The present invention relates to a kind of working method of Al-Cu-Mg alloy, refering in particular to is a kind of method of the Al-Cu-Mg of raising Alloy Anti fatigue property; Belong to Nonferrous Metal Forming technical field.
Technical background
Al-Cu-Mg is associated gold owing to having medium tenacity, and good toughness and excellent anti-fatigue performance, be the precipitation hardenable aluminium alloy of widespread use in aerospace, especially usually, as the application of aircraft skin material, at aviation field, has extremely important status.Yet the fast development of matrix material has in recent years brought larger impact to aluminium alloy, therefore further improve this Fatigue Properties of Aluminum Alloy significant.
Research shows, for the raising of this aluminium alloy anti-fatigue performance, has mainly carried out at present aspect researchs such as alloy impurity element, elementide size, predeformation, Cu-Mg composition ratio, superfluous phase, electrical effect, has obtained larger breakthrough.Research shows that the Al-Cu-Mg alloy of low Cu/Mg composition ratio has more excellent anti-fatigue performance.Under the Al-Cu-Mg alloy natural aging state of low Cu/Mg composition ratio, the precipitation phase of the Precipitation of alloy in GPB district.The atom segregation cluster that natural aging is separated out is proved to be the past multiple slip that is conducive to CYCLIC LOADING process Dislocations, thereby falls low-alloyed fatigue damage.In addition, superfluous phase, impurity, temperature are to elementide size, and the electrical effect of atom segregation and predeformation are introduced dislocation relevant research has also been done in the aspects such as impact of slippage under repeated stress.
Yet above-mentioned many research is some aspects that Fatigue Properties of Aluminum Alloy improves.Analysis shows, under alloy fatigue performance and repeated stress effect, the reciprocal slippage of dislocation has direct relation.The obstruction that dislocation glide is subject to is larger, and fatigue damage accumulation is faster, and spreading rate will be higher.Research shows, the particular orientation of dislocation glide and alloy grain has direct relation, and the crystal grain with goss texture can increase the crack closure effect of alloy, thereby reduces crack growth rate.In contrast, such as modulated structures such as brass, easily make collapse crystal boundary expansion of crackle, be unfavorable for carrying heavy alloyed anti-fatigue performance.Research at present shows, by techniques such as process annealing, high temperature solid solutions, can obtain to a certain extent highdensity goss texture, and can also suppress the generation such as deformation textures such as brass simultaneously.The appearance of these techniques can improve the anti-fatigue performance of such alloy to a certain extent, yet the goss texture density of its acquisition is generally speaking all lower, also has larger room for promotion.In addition these technical matters are all comparatively complicated comparatively speaking, need to expend the more energy, and industrial production is inconvenience very.
How obtaining stronger goss texture or elimination (or at utmost weakening) modulated structure is the key point that improves this series alloys anti-fatigue performance.Therefore, develop suitable aluminum alloy heat complete processing, eliminate or weaken brass texture the stronger goss texture of acquisition in alloy, and can eliminate the thick phase in alloy simultaneously, reducing crack initiation probability, is the effective way that improves this series alloys anti-fatigue performance.By being conducive to, promote this series alloys at the application level tool of aerospace field, there is far-reaching realistic meaning.
Summary of the invention
The method that the object of the invention is to overcome the deficiency of prior art and simple, easy to operate, the cost-saving raising Al-Cu-Mg Alloy Anti fatigue property of a kind of technique is provided; Further to improve the anti-fatigue performance after existing aluminum alloy materials thermal treatment.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, is that the Al-Cu-Mg alloy after homogenizing is processed carries out high temperature hot rolling successively, a solution treatment, and aximal deformation value is cold rolling, Secondary Solid Solution Treatment, natural aging treatment.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, described high temperature hot rolling technology is: 430-490 ℃ of hot-rolled temperatures, soaking time 20 minutes-4 hours, hot rolling deformation amount 30-60%.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, a described solution treatment, Secondary Solid Solution Treatment technique are: 470-500 ℃ of solid solubility temperatures, soaking time 5 minutes-2 hours, shrend.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, described aximal deformation value cold-rolling process is: cold rolling reduction 50%-90%.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, described Secondary Solid Solution Treatment adopts salt bath heating.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, described natural aging is to place at normal temperatures 50-200 hour.
A kind of method that improves Al-Cu-Mg Alloy Anti fatigue property of the present invention, in Al-Cu-Mg alloy, each constituent mass percentage composition is: Cu3.0-4.9%, Mg1.0-1.8%, Mn0.3-1.0, surplus is Al.
Mechanism of the present invention and advantage sketch under:
The present invention makes alloy generation dynamic recrystallization by high temperature hot rolling technology, alloy dynamic recrystallization in the operation of rolling is fully completed, thereby form the more recrystallization texture such as Goss, Cube etc. with certain orientation.And the powers of texture such as Goss, Cube and the fatigue property of material have direct relation.The alloy that goss texture is stronger, it is more in crystal grain that { 111} face is in or close to the additional shearing stress direction of maximum, be conducive to the past multiple slip of dislocation, make alloy more easily produce resident slip band, thereby the plasticity that strengthens fatigue cracking is induced closed effect, reduce damage accumulation, and promote crack deflection, and then low-alloyed fatigue crack growth rate falls, effectively carry heavy alloyed anti-fatigue performance.
Adopt cold rolling front solution treatment, can make the thick second phase particles except Fe, Si impurity be able to back dissolving, avoid high energy region to form, thereby be conducive to eliminate the generation of inhomogeneous recrystallize, avoid the formation of inhomogeneous recrystallize; Because inhomogeneous recrystallize be formed with the generation that is beneficial to the modulated structures such as Brass, the existence of this texture, can there is the expansion of cross-border boundary in fatigue cracking, be unfavorable for improving fatigue property.Therefore cold rolling front solution treatment can further improve the anti-fatigue performance of material.
Larger cold rolling of deflection subsequently, is conducive to make a large amount of dislocations of material production, and dislocation interactions strengthens, and easily forms piling up of dislocations, dislocation is completed a business transaction, and forms larger energy storage, and Recrystallization nucleation speed is strengthened, formation small grains.Fatigue cracking needs to pass through more crystal boundary under small grains, hinders greatly, and crack growth rate is lower, is conducive to the raising of fatigue property.
Last salt bath high temperature, short time solution treatment, is conducive to the formation of recrystallization texture, and its some orientation (such as Goss, Cube) is stronger, is more conducive to the fatigue property of material.
In sum, technique advantages of simple of the present invention, by modes such as high temperature hot rolling and cold rolling front solid solutions, makes alloy obtain highdensity Goss texture and is conducive to dislocation toward multiple slip and promotes the crystal grain of fatigue crack closure to distribute.Make Al-Cu-Mg alloy there is higher anti-fatigue performance, be applicable to industrial applications.
Accompanying drawing explanation
Accompanying drawing 1 is the Fatigue Crack Growth Rates curve of the embodiment of the present invention 2,3,6,7
Accompanying drawing 2 is metallographic structures that during the embodiment of the present invention 2 adopts, warm rolling+cold rolling after annealing+solution hardening aging technique is processed.
Accompanying drawing 3 is metallographic structures that warm rolling during the embodiment of the present invention 3 adopts+cold rolling front solid solution+solution hardening aging technique is processed.
Accompanying drawing 4 is that the embodiment of the present invention 6 adopts the metallographic structure that high temperature hot rolling+cold rolling after annealing+solution hardening aging technique is processed.
Accompanying drawing 5 is that the embodiment of the present invention 7 adopts the metallographic structure that high temperature hot rolling+cold rolling front solid solution+solution hardening aging technique is processed.
Accompanying drawing 6 is orientation distribution function figure that during the embodiment of the present invention 2 adopts, warm rolling+cold rolling after annealing+solution hardening aging technique is processed.
Accompanying drawing 7 is orientation distribution function figure that warm rolling during the embodiment of the present invention 3 adopts+cold rolling front solid solution+solution hardening aging technique is processed.
Accompanying drawing 8 is that the embodiment of the present invention 6 adopts the orientation distribution function figure that high temperature hot rolling+cold rolling after annealing+solution hardening aging technique is processed.
Accompanying drawing 9 is that the embodiment of the present invention 7 adopts the orientation distribution function figure that high temperature hot rolling+cold rolling front solid solution+solution hardening aging technique is processed.
In Fig. 1:
Curve A is the Fatigue Crack Growth Rates curve of embodiment 2, and treatment process is: in warm rolling+cold rolling after annealing+solution hardening timeliness;
Curve B is the Fatigue Crack Growth Rates curve of embodiment 3, and treatment process is: in warm rolling+cold rolling front solid solution+solution hardening timeliness;
Curve C is the Fatigue Crack Growth Rates curve of embodiment 6, and treatment process is: high temperature hot rolling+cold rolling after annealing+solution hardening timeliness;
Curve D is the Fatigue Crack Growth Rates curve of embodiment 7, and treatment process is: high temperature hot rolling+cold rolling front solid solution+solution hardening timeliness;
As can be seen from Figure 1, the alloy phase of processing through high temperature hot rolling provided by the invention in the spreading rate of the warm alloy that rolls processing obviously lower, the fracture toughness property of alloy and fatigue resistance can improve largely, as embodiment 7 and embodiment 3 or embodiment 6 and embodiment 2;
Through the alloy fatigue performance of cold rolling front solution treatment also apparently higher than the alloy that there is no solution treatment before cold rolling, as embodiment 7 and embodiment 6 or embodiment 3 and embodiment 2.
From Fig. 2-5, can find out, the alloy phase that high temperature hot rolling is processed in the warm alloy microstructure that rolls processing comparatively tiny, be even under other art breading about half of grain-size.To a certain degree, crystal grain is more tiny, and fatigue crack growth is hindered, and reduces Fatigue Crack Growth Rates, and meanwhile crystal grain thinning improves alloy strength.
From Fig. 6-9, the alloy goss texture density (3.72) of processing through high temperature hot rolling is improved, and the rolling textures such as brass reduce, and fatigue property is improved.
Embodiment
Below in conjunction with the drawings and specific embodiments, the invention will be further described.
Mechanical Properties of Aluminum Alloys after embodiment of the present invention 1-9 processes is in Table 1.
Embodiment 1
By alloying constituent, be: 3.8%Cu, 1.0%Mg, 0.3%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 70% deflection 430 ℃ of insulations after 1 hour, then after 470 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 80% deflection, then carry out natural aging treatment after 470 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 456MPa, and yield strength is 327MPa, and unit elongation is 23%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.00595mm/cycle.
Embodiment 2
By alloying constituent, be: 4.4%Cu, 1.3%Mg, 0.45%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 70% deflection 440 ℃ of insulations after 1 hour, carry out afterwards the cold rolling of 80% deflection, then carry out 400 ℃ of anneal 1h, again carry out afterwards natural aging treatment after 490 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 476MPa, and yield strength is 334MPa, and unit elongation is 23.2%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.00335mm/cycle.
Embodiment 3
By alloying constituent, be: 4.9%Cu, 1.5%Mg, 0.8%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 70% deflection 440 ℃ of temperature after 1 hour, then after 490 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 80% deflection, again carry out afterwards natural aging treatment after 490 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 475MPa, and yield strength is 331MPa, and unit elongation is 22.3%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0043mm/cycle.
Embodiment 4
By alloying constituent, be: 3.8%Cu, 1.8%Mg, 1.0%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection 450 ℃ of insulations after 1 hour, then after 480 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 90% deflection, carry out afterwards natural aging treatment after 480 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 465MPa, and yield strength is 320MPa, and unit elongation is 22%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0049mm/cycle.
Embodiment 5
By alloying constituent, be: 3.8%Cu, 1.0%Mg, 0.3%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection 460 ℃ of insulations after 1 hour, then after 480 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 90% deflection, carry out afterwards natural aging treatment after 480 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 477MPa, and yield strength is 330MPa, and unit elongation is 22%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0055mm/cycle.
Embodiment 6
By alloying constituent, be: 3.8%Cu, 1.0Mg, 0.45%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection after in the time of 490 ℃, carry out afterwards the cold rolling of 90% deflection, carry out 400 ℃ of anneal 1h, finally carry out natural aging treatment after 490 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 488.5MPa, and yield strength is 335MPa, and unit elongation is 25.03%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0029mm/cycle.
Embodiment 7
By alloying constituent, be: 3.8%Cu, 1.3%Mg, 0.45%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection 490 ℃ of insulations after 1 hour, then after 490 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 90% deflection, carry out afterwards natural aging treatment after 490 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 493.6MPa, and yield strength is 338MPa, and unit elongation is 24.33%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.00187mm/cycle.
Embodiment 8
By alloying constituent, be: 4.5%Cu, 1.8Mg, 0.9%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection 480 ℃ of insulations after 1 hour, then after 470 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 90% deflection, carry out afterwards natural aging treatment after 470 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 480MPa, and yield strength is 332MPa, and unit elongation is 25%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0069mm/cycle.
Embodiment 9
By alloying constituent, be: 4.9%Cu, 1.8%Mg, 1.0%Mn, surplus is that after the Al-Cu-Mg alloy homogenizing of Al, ingot casting directly carries out the hot rolling of 50% deflection 490 ℃ of insulations after 1 hour, then after 490 ℃ of air solution treatment shrend in 1 hour, carry out the cold rolling of 90% deflection, carry out afterwards natural aging treatment after 490 ℃ of salt bath solid solutions shrend in 20 minutes.Tensile strength is 470MPa, and yield strength is 330MPa, and unit elongation is 23%.As stress spreading factor Δ K=33MPa*m
1/2time, the spreading rate of alloy is respectively 0.0070mm/cycle.
The mechanical property contrast of table 1 alloy of the present invention
| Embodiment | σ b/MPa | σ 0.2/MPa | δ/%da/dN（mm/cycle） |
| Embodiment 1 | 456.0 | 327.0 | 23.0(△K=33MPa*m 1/2)0.00595 |
| Embodiment 2 | 475.0 | 331.0 | 22.3(△K=33MPa*m 1/2)0.00335 |
| Embodiment 3 | 476.0 | 334.0 | 23.2(△K=33MPa*m 1/2)0.00432 |
| Embodiment 4 | 465.0 | 320.0 | 22.0(△K=33MPa*m 1/2)0.0049 |
| Embodiment 5 | 477.0 | 333.0 | 22.0(△K=33MPa*m 1/2)0.0055 |
| Embodiment 6 | 488.5 | 335.0 | 25.3(△K=33MPa*m 1/2)0.0029 |
| Embodiment 7 | 493.6 | 338.0 | 24.3(△K=33MPa*m 1/2)0.00187 |
| Embodiment 8 | 480.0 | 332.0 | 25.0(△K=33MPa*m 1/2)0.0069 |
| Embodiment 9 | 470.0 | 330.0 | 23(△K=33MPa*m 1/2)0.0070 |
Thermal treatment process provided by the invention has not only improved the intensity of alloy as can be seen from Table 1, and obviously carries heavy alloyed fracture toughness property and anti-fatigue performance, widens its range of application.
Claims (7)
1. improving a method for Al-Cu-Mg Alloy Anti fatigue property, is that the Al-Cu-Mg alloy after homogenizing is processed carries out high temperature hot rolling successively, a solution treatment, and aximal deformation value is cold rolling, Secondary Solid Solution Treatment, natural aging treatment.
2. a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property according to claim 1, is characterized in that: described high temperature hot rolling technology is: 430-490 ℃ of hot-rolled temperatures, soaking time 20 minutes-4 hours, hot rolling deformation amount 30-60%.
3. a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property according to claim 1, is characterized in that: a described solution treatment, Secondary Solid Solution Treatment technique are: 470-500 ℃ of solid solubility temperatures, soaking time 5 minutes-2 hours, shrend.
4. a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property according to claim 1, is characterized in that: described aximal deformation value cold-rolling process is: cold rolling reduction 50%-90%.
5. a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property according to claim 1, is characterized in that: described Secondary Solid Solution Treatment adopts salt bath heating.
6. according to a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property described in claim 1-5 any one, it is characterized in that: described natural aging is to place at normal temperatures 50-200 hour.
7. a kind of method that improves Al-Cu-Mg Alloy Anti fatigue property according to claim 6, is characterized in that: in Al-Cu-Mg alloy, each constituent mass percentage composition is: Cu3.0-4.9%, and Mg1.0-1.8%, Mn0.3-1.0%, surplus is Al.
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| CN109898000A (en) * | 2019-03-29 | 2019-06-18 | 郑州轻研合金科技有限公司 | A kind of super high strength heat resistant alloy and preparation method thereof |
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