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Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure

A technology with high thermal stability and processing method, which is applied in the field of high-strength anti-fatigue microstructure processing, can solve the problems of accelerated fatigue crack growth, difficult recovery movement of alloys, uniform deformation of fatigue crack tip, etc., and achieves delayed degradation and excellent fatigue resistance. Effect

Inactive Publication Date: 2010-05-19
CENT SOUTH UNIV
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  • Summary
  • Abstract
  • Description
  • Claims
  • Application Information

AI Technical Summary

Problems solved by technology

Studies have shown that artificial aging or long-term heat exposure will cause the precipitation of equilibrium phases in naturally-aged alloys, which are generally difficult to be cut by dislocations, which makes it difficult for dislocations to recover and cause fatigue crack tips during cyclic deformation of the alloy. Uniform deformation thus accelerates fatigue crack growth

Method used

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  • Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure
  • Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure
  • Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure

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Experimental program
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Effect test

Embodiment 1

[0016] The alloy composition is: 4.0% Cu, 1.2% Mg, 0.6% Mn, 0.2% Ti, and the balance is Al 2524 aluminum alloy plate is solid-dissolved at 490°C for 1 hour and water quenched, and then aged at 170°C for 50 minutes. Mechanical properties at room temperature after this treatment: tensile strength is 462MPa, yield strength is 326MPa, elongation is 27%; after heat exposure at 135°C / 1000 hours, the tensile strength of the alloy is 472MPa, yield strength is 410MPa , the elongation is 14%; after 100°C / 2000 hours of heat exposure, the tensile strength of the alloy is 484MPa, the yield strength is 333MPa, and the elongation is 19%. The fatigue crack growth rate of the original state alloy by this treatment method is lower than that of the T351 state alloy; after heat exposure, the fatigue crack growth rate of the alloy treated by this treatment method is still lower than that of the T351 treated alloy after heat exposure.

Embodiment 2

[0018] The alloy composition is: 4.0% Cu, 1.2% Mg, 0.6% Mn, 0.2% Ti, and the balance is Al in solid solution for 1.5 hours at 500°C and water quenched, and then aged at 185°C for 30 minutes. Mechanical properties after this treatment: the tensile strength of the alloy at room temperature is 461MPa, the yield strength is 333MPa, and the elongation is 26.8%; after heat exposure at 135°C / 1000 hours, the tensile strength of the alloy at room temperature is 470.9MPa , the yield strength is 409MPa, and the elongation is 15.8%; after 100℃ / 2000 hours of heat exposure, the tensile strength of the alloy at room temperature is 484MPa, the yield strength is 333MPa, and the elongation is 22%. The fatigue crack growth rate of the original state alloy by this treatment method is lower than that of the T351 state alloy; after heat exposure, the fatigue crack growth rate of the alloy treated by this treatment method is still lower than that of the T351 treated alloy after heat exposure.

Embodiment 3

[0020] The alloy composition is: 4.0% Cu, 1.2% Mg, 0.6% Mn, 0.2% Ti, and the balance is Al. The aluminum alloy plate is solid-dissolved at 500°C for 1 hour and quenched in water, and then aged at 200°C for 30 minutes. The mechanical properties after this treatment: the tensile strength of the alloy at room temperature is 466MPa, the yield strength is 344MPa, and the elongation is 25.2%; after heat exposure at 135°C / 1000 hours, the tensile strength of the alloy at room temperature is 468MPa, The yield strength is 398MPa, and the elongation is 15.4%. After 100°C / 2000 hours of heat exposure, the tensile strength of the alloy at room temperature is 510MPa, the yield strength is 384MPa, and the elongation is 21%. The fatigue crack growth rate of the original state alloy by this treatment method is lower than that of the T351 state alloy; after heat exposure, the fatigue crack growth rate of the alloy treated by this treatment method is still lower than that of the T351 treated alloy...

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Abstract

The present invention discloses one heat treating process for aluminum alloy to obtain anitfatigue microstructure with high heat stability. The treating process for aluminum alloy plate includes the first solution treatment at 490-500 deg.c, and the subsequent artificial ageing treatment at 170-200 deg.c for 20-60 min. The heat treating process makes the Al-Cu-Mg alloy obtain reinforcing GPB structure in relatively large size, excellent antifatigue performance, delayed degradation of the antifatigue performance and anitfatigue microstructure with high heat stability.

Description

technical field [0001] The invention relates to a processing method for aluminum alloy, in particular to a processing method for obtaining a microstructure with high thermal stability, high strength and anti-fatigue for Al-Cu-Mg alloy. Background technique [0002] Al-Cu-Mg alloys with low Cu / Mg ratio are widely used in aerospace due to their moderate strength, good toughness and excellent fatigue properties. The aging precipitation sequence of this series of alloys is: GPB zone, S′ phase, S phase. According to different service conditions, the heat treatment state of the alloy is also different, so the microstructure state in the alloy is also different. The aging state of the alloy used as a damage-resistant component is generally the natural aging state, that is to say, the microstructure of the alloy is in the GPB zone stage of aging precipitation. Literature studies have shown that the slip occurring in multiple slip systems of pure aluminum alloys is irreversible due...

Claims

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Application Information

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Patent Type & Authority Patents(China)
IPC IPC(8): C22F1/04
Inventor 刘志义刘延斌李云涛
Owner CENT SOUTH UNIV
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