Properties of clad sheets
The effect of full heat treatment includes the effect of hardening and aging effect. Different aluminum alloys the influence of quenching and aging on the strength of different.
Aging
This process, when the alloy after quenching without polymorphic transformation is the decomposition of the supersaturated solid solution. The phenomenon of aging of aluminum alloys was opened by the Wilm. He found that an alloy of aluminum with copper and magnesium, tempered at 500 °C in water, after four days of standing at room temperature became stronger and stronger, without losing ductility. When heated, the aging process accelerates. From duralumin alloys, the greatest effect of the heat treatment of the alloy D16. Aging, running at normal temperatures, adopted the term «natural aging» and aging in the special conditions of heating after quenching — «artificial aging». Structural transformations during aging need to be explained. The decomposition of the solid solution is usually in three stages. 1) Education coherent with the matrix, GP zones (by Guinier-Preston), 2) formation of partially coherent metastable phases, 3) the formation of incoherent particles of the stable phase. Some alloys will not age at room temperature and to ageing, require a special heater. Other alloys of the transition from natural to artificial aging (i.e., from zones to the phases) occurs at room temperature, however, at very long exposures.
Aging of aluminum
Naturally aged alloys of aluminum while maintaining ductility have less strength compared with the annealed alloys. The fact that at 20−100°C hardening occurs due to the formation of GP zones, while at higher temperatures there is a selection of metastable phase S' (stable S-Al2 CuMg). Further increase in temperature and the aging time leads to coagulation of metastable phases and loss of strength. In industrial production for the delivery and assessment of the quality of the alloy D16 is accelerated aging at 100 °C for several hours (not waiting the four days of the completion of the natural aging at room temperature). This is justified as in both cases a comparable process of aging and conditioning is achieved the same strength. This limits separation of the particles of metastable phases that reduce the corrosion resistance.
The strength of the clad sheets (transverse to rolling) | |||||
---|---|---|---|---|---|
Alloy | The state of the sheets | The thickness of the sheets, mm |
σin | σ 0,2 | β, % |
kgf/mm2 | |||||
D1 | Annealed | 0,6−1,9 | to 23 | - | 12 |
2,0−10,0 | to 24 | - | |||
Hardened and naturally aged | 0,5−1,9 | 37 | 19 | 15 | |
2,0−10,0 | 38 | 20 | |||
D16 | Annealed | 0,5−1,9 | to 23 | - | 10 |
2,0−10,0 | to 24 | - | |||
Hardened and naturally aged | 0,5−1,9 | 41,5 | 27,5 | 13 | |
2,0−6,0 | 43,5 | 28 | 11 | ||
6,1 — 10,0 | 10 | ||||
Cold-worked after quenching and naturally aged | 1,5−1,9 | 43,5 | 34 | 10 | |
2,0−7,5 | 46,5 | 35 | 8 | ||
Hardened and artificially aged | 0,5−0,7 | 40,0 | 35 | 5 | |
0,8−1,9 | 43,5 | 38 | |||
2,0−6,0 | 45,5 | 39 | |||
Cold-worked after quenching and artificially aged | 1,5−1,9 | 46 | 43 | 3 | |
2,0−6,0 | 49 | 46 | 4 | ||
D19 | Annealed | 0,5−1,9 | to 23 | - | 10 |
2,0−10,0 | to 24 | - | |||
Hardened and naturally aged | 0,5−1,9 | 40,5 | 26,5 | 13 | |
2,0−6,0 | 42,5 | 27 | 11 | ||
6,1 — 10,0 | 10 | ||||
Cold-worked after quenching and natural aging | 1,5−1,9 | 43,5 | 34 | 10 | |
2,0−7,5 | 46,5 | 35 | 8 |
Note:
σв: temporary resistance, MPa (kgf/mm2)
σ0,2: yield strength, MPa (kgf/mm2)
β: the relative elongation in %
The strength of extruded bars | ||||||
---|---|---|---|---|---|---|
Grade | Condition when the manufacture |
Condition when test |
Ø mm | σin | σ0,2 not less than |
β, % |
MPa (kgf/mm2) | ||||||
D1 | Without heat treatment | Without heat treatment | 8−300 | 195 (20) | 110 (11) | 12 |
Tempered and naturally aged | 8−130 | 375 (38) | 215 (22) | |||
130−300 | 355 (36) | 195 (20) | 10 | |||
Tempered and naturally aged | Tempered and of course aged |
8−100 | 375 (38) | 215 (22) | 12 | |
D16 | Without heat treatment | Without heat treatment | 8−300 | 245 (25) | 120 (12) | |
Tempered and of course aged |
8−22 | 390 (40) | 275 (28) | 10 | ||
22−130 | 420 (43) | 295 (30) | ||||
130−300 | 410 (42) | 275 (28) | 8 | |||
300−400 | 390 (40) | 245 (25) | 6 | |||
Tempered and of course aged |
Tempered and of course aged |
8 — 22 | 390 (40) | 275 (28) | 10 | |
22 — 100 | 420 (43) | 296 (30) |
The strength of the pipes in quenched and naturally aged condition | ||||||
---|---|---|---|---|---|---|
Alloy | A method of manufacturing | Parameters mm | σin | σ0,2 | δ, % | |
Wall thickness | Ø | kgf/mm2 | ||||
Not less than | ||||||
D1 | Extruded | ≤5 | - | 34 | - | 10 |
≥5 | ≤120 | 36 | 20 | 12 | ||
более120 | 38 | 22 | 10 | |||
Rolled and pulled | to 1.0 | ≤22 | 38 | 20 | 13 | |
1,5−6 | 14 | |||||
to 1.0 | 23−50 | 40 | 23 | 12 | ||
1,5−5 | 13 | |||||
more than 5 | more than 50 | 11 | ||||
D19 | Extruded | ≤5 | 37 | - | 9 | |
≥5 | ≤120 | 40 | 26 | 12 | ||
более120 | 43 | 28 | 10 | |||
Rolled and pulled | to 1.0 | ≤22 | 42 | 26 | 13 | |
1,5−5 | 14 | |||||
≥5 | 23−50 | 43 | 29 | 12 | ||
50 | 10 |
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