Properties of clad sheets.
The effect of a complete heat treatment includes a quenching effect and an aging effect. The effects of quenching and aging on strength are different for different aluminum alloys.
Aging effect
This is the process whereby the supersaturated solid solution dissolves in an alloy after quenching without a polymorphic transformation. The aging phenomenon of aluminum alloys was discovered by Wilm. He found that an alloy of aluminium with copper and magnesium that had been quenched at 500°C in water became stronger and harder after four days of exposure (t° 50°C) without loss of ductility. Heating accelerated the aging process. Of the dural alloys, alloy D16 had the greatest effect of heat treatment. The term "natural aging" is accepted for aging without special heating and "artificial aging" for aging under special heating after quenching. The structural transformations during aging need to be explained. The decomposition of solid solution usually proceeds in three stages. 1) formation of coherent with matrix GP zones (Guinier-Preston), 2) formation of partially coherent metastable phases, 3) formation of incoherent particles of stable phase. Some alloys do not age at room temperature and require special heating to start aging. In other alloys, the transition from natural to artificial aging (i.e., from zones to phases) also occurs at room temperature, although at very long dwell times.
Aging of duralumin
Natural aging of duralumin achieves high ductility but less strength compared to annealed alloys. The fact is that the temperature of 20-100°C gives hardening due to the formation of GP zones, and at higher temperatures there is a release of metastable phase S', (stable S-Al2 CuMg). Further increase in temperature and aging time leads to coagulation of metastable phases and a decrease in strength. In industrial production for acceptance and quality assessment, alloy D16 undergoes accelerated aging at 100 °C for several hours. This is justified because in both cases a similar zone aging process takes place and a similar strength is achieved. At the same time there is a release of particles of metastable phases along the boundaries, which reduces the corrosion resistance.
Strength of clad plates (crosswise rolling)
| Alloy | Condition of sheets | Plate thickness, mm | σ in | σ 0,2 | β, % |
|---|---|---|---|---|---|
| Д1 | Annealed | 0,6-1,9 | up to 23 | - | 12 |
| Д1 | Annealed | 2,0-10,0 | up to 24 | - | 12 |
| Д1 | Hardening and natural aging | 0,5-1,9 | 37 | 19 | 15 |
| Д1 | Hardening and natural aging | 2,0-10,0 | 38 | 20 | 15 |
| Д16 | Annealed | 0,5-1,9 | up to 23 | - | 10 |
| Д16 | Annealed | 2,0-10,0 | up to 24 | - | 10 |
| Д16 | Hardening and natural aging | 0,5-1,9 | 41,5 | 27,5 | 13 |
| Д16 | Hardening and natural aging | 2,0-6,0 | 43,5 | 28 | 11 |
| Д16 | Hardening and natural aging | 6,1 - 10,0 | 43,5 | 28 | 10 |
| Д16 | Annealed after hardening and naturally aged | 1,5-1,9 | 43,5 | 34 | 10 |
| Д16 | Annealed after hardening and naturally aged | 2,0-7,5 | 46,5 | 35 | 8 |
| Д16 | Hardened and artificially aged | 0,5-0,7 | 40,0 | 35 | 5 |
| Д16 | Hardened and artificially aged | 0,8-1,9 | 43,5 | 38 | 5 |
| Д16 | Hardened and artificially aged | 2,0-6,0 | 45,5 | 39 | 5 |
| Д16 | Naturalized after hardening and artificially aged | 1,5-1,9 | 46 | 43 | 3 |
| Д16 | Annealed after hardening and artificially aged | 2,0-6,0 | 49 | 46 | 4 |
| Д19 | Annealed | 0,5-1,9 | to 23 | - | 10 |
| Д19 | Annealed | 2,0-10,0 | up to 24 | - | 10 |
| Д19 | Hardened and naturally aged | 0,5-1,9 | 40,5 | 26,5 | 13 |
| Д19 | Hardened and naturally aged | 2,0-6,0 | 42,5 | 27 | 11 |
| Д19 | Hardened and naturally aged | 6,1 - 10,0 | 42,5 | 27 | 10 |
| Д19 | Natural annealed after quenching and natural aging | 1,5-1,9 | 43,5 | 34 | 10 |
| Д19 | Natural annealed after quenching and natural aging | 2,0-7,5 | 46,5 | 35 | 8 |
Note:
σv: tensile strength, MPa (kgf/mm²)
σ0.2: yield strength, MPa (kgf/mm²)
β: % elongation.
Strength of pressed bars
| Alloy grade | State during fabrication | State upon test | Ø mm | σ in | σ0,2 | β, % |
|---|---|---|---|---|---|---|
| Д1 | Without heat treatment | Without heat treatment | 8-300 | 195 (20) | 110 (11) | 12 |
| Д1 | Without heat treatment | Hardened and naturally aged | 8-130 | 375 (38) | 215 (22) | 12 |
| Д1 | Without heat treatment | Hardened and naturally aged | 130-300 | 355 (36) | 195 (20) | 10 |
| Д1 | Hardened and naturally aged | Hardened and naturally aged | 8-100 | 375 (38) | 215 (22) | 12 |
| Д16 | Without heat treatment | Without heat treatment | 8-300 | 245 (25) | 120 (12) | 12 |
| Д16 | Without heat treatment | Quenched and natural aging | 8-22 | 390 (40) | 275 (28) | 10 |
| Д16 | Without heat treatment | Quenched and natural aging | 22-130 | 420 (43) | 295 (30) | 10 |
| Д16 | Without heat treatment | Quenched and natural aging | 130-300 | 410 (42) | 275 (28) | 8 |
| Д16 | 300-400 | Hardening and natural aging | 390 (40) | 245 (25) | 6 | |
| Д16 | Hardening and natural aging | Hardening and natural aging | 8 - 22 | 390 (40) | 275 (28) | 10 |
| Д16 | Hardened and naturally aged | Hardened and naturally aged | 22 - 100 | 420 (43) | 296 (30) | 10 |
Hardened and naturally aged pipe strength
| Alloy | Production method | Wall thickness | Ø | σ in | σ0,2 | δ, % |
|---|---|---|---|---|---|---|
| Д1 | Pressed | ≤5 | - | 34 | - | 10 |
| Д1 | Pressed | ≥5 | ≤120 | 36 | 20 | 12 |
| Д1 | Pressed | ≥5 | over 120 | 38 | 22 | 10 |
| Д1 | Rolled and drawn | up to 1.0 | ≤22 | 38 | 20 | 13 |
| Д1 | Rolled and drawn | 1,5-6 | ≤22 | 38 | 20 | 14 |
| Д1 | Rolled and drawn | up to 1.0 | 23-50 | 40 | 23 | 12 |
| Д1 | Rolled and drawn | 1,5-5 | 23-50 | 40 | 23 | 13 |
| Д1 | Rolled and drawn | over 5 | more than 50 | 40 | 23 | 11 |
| Д19 | Pressed | ≤5 | 37 | - | 9 | |
| Д19 | Pressed | ≥5 | ≤120 | 40 | 26 | 12 |
| Д19 | Pressed | ≥5 | over 120 | 43 | 28 | 10 |
| Д19 | Rolled and drawn | up to 1.0 | ≤22 | 42 | 26 | 13 |
| Д19 | Rolled and drawn | 1,5-5 | ≤22 | 42 | 26 | 14 |
| Д19 | Rolled and drawn | ≥5 | 23-50 | 43 | 29 | 12 |
| Д19 | Rolled and drawn | ≥5 | 50 | 43 | 29 | 10 |
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