Fatigue, Fracture and Microstructure Relationships of an Aluminum Automobile Component

Aluminum alloys are progressively used in the automobile industry due to several advantages such as low specific weight, good formability, good corrosion resistance and a nice surface appearance. The standard production forming processes such as extrusion and forging, can give rise to large variations in the tensile, fatigue and fracture properties. In AlMgSi alloys (6061, 6062, 6060 and 6082), yield stress have been shown to have only a weak dependence on grain size. However, a large part of the variations in other properties can be traced back to differences in grain size.

Production of Universal Joints. Cold forged products are strong, tolerances are tight and strength/ductility can be optimized by tempering Joints having different grain morphologies are made from two conditions of alloy AA 6082: Alloy A which is rich in Mg and the low Mg containing alloy B also specified with Cr. Three different forging and heat treatments are employed to obtain different grain structures in the alloy A. The alloy B series is similarly produced as Series 1 of the alloy A. All series are artificially aged to the T6 condition. After forging the joints are machined to the shown geometry. A parallel set of joints is machined with a serrated attachment hole.

Characterization of Joints. Metallographic characterization is carried out in scanning (SEM) and transmission electron microscopes (TEM). Tensile specimens are taken from the joint arm, two specimens from each joint. Fatigue life tests are conducted at a fully reversed torsion moment of ±70Nm at 10Hz in moist air environment.

Characterization of laboratory material. Additional laboratory investigations involve five different grain morphologies in the alloy A (T6 temper). Fatigue life is determined from 3-5 electropolished specimens of each condition at R = -1 and 20 Hz. Further, fracture toughness in terms of K, is characterized by loading 9.5 mm diameter short rod specimens (W=14.5 mm, t = 0.2 mm) in a servohydraulic MTS machine. The specimen geometry and test performance is in accordance with the proposed ASTM standard.

Fatigue and mechanical properties of universal Joints. The alloy B series and Series 1 of the alloy A have a larger elongation at fracture (ef), than the two other series (Table 1). The average fatigue life tends to be longer in Series 2 and 3 than in the other series. Joints having serrated attachment holes have the fatigue life lowered by a factor ranging between 2 and 14 when compared to the smooth hole geometry, and all fatigue cracks are initiated in serrations. An important observation is that the microstructures of Series 2 and 3 and the alloy B, seem to be more notch sensitive with respect to fatigue than the Series 1. Furthermore, enhanced fatigue life of the relatively coarse grained joints with serrated holes (alloy B and Series 1), may be due to roughness induced crack closure reducing the crack driving force.

Alloys with precipitate free zones (PFZ), as with the alloy B and Series 1, have been shown to generate higher closure levels than alloys without PFZ.

Microstructure of universal Joints. The most significant variation in the microstructure due to changes in the heat treatment/deformation procedure is in the grain structure morphology. Series 1 of the alloy A has a partly elongated recrystallized structure, i.e. 40 μm high vs. 60 μm long. Series 2 and 3 are both unrecrystallized having a short and a long fiber-shaped structure respectively. The alloy B series has a recrystallized almost equiaxed grain structure, -140 μm in diameter.

SEM particle analyses show that the alloy B series has less of the small (-1 μm) and significantly more of the coarse (>5 μm) particles than Series 1. This can contribute to the formation of a coarse grain structure in the alloy B.

TEM studies show that Series 2 and 3 have both a higher dislocation density and a coarser precipitate structure than Series 1, i.e. slightly overaged. These two facts may govern the lower the tensile ductility and the increased fatigue notch sensibility in the Series 2 and 3.

Correlation to laboratory material data. In general, the laboratory materials show better tensile properties than the joints. Taking into account the observed coarse precipitate structures in the joints, i.e. Series 2 and 3, the lower strength and ductility of these joints are probably due to overaging effects.

The non-recrystallized fiber structure has the highest fracture toughness. Further, the recrystallized (50 μm) and the deformed fiber structure show a significantly lower K, than the undeformed fiber structure.

From the smooth specimen S-N curves of the five laboratory conditions, it is easily seen that the non-recrystallized fiber structure has better fatigue resistance than the recrystallized structure. This is in agreement with the fatigue life data of the joints.

Conclusions