Abstract A land-grid array connector, electrically connecting an array of plated contact pads on a ceramic substrate chip carrier to plated contact pads on a printed circuit board (PCB), failed in a year after assembly due to time-delayed fracture of multiple C-shaped spring connectors. The land-grid-array connectors analyzed had arrays of connectors consisting of gold on nickel plated Be-Cu C-shaped springs in compression that made electrical connections between the pads on the ceramic substrates and the PCBs. Metallography, fractography and surface analyses revealed the root cause of the C-spring connector fracture to be plating solutions trapped in deep grain boundary grooves etched into the C-spring connectors during the pre-plating cleaning operation. The stress necessary for the stress corrosion cracking mechanism was provided by the C-spring connectors, in the land-grid array, being compressed between the ceramic substrate and the printed circuit board.

Abstract In this study, a comprehensive investigation of the Ag-Al bond degradation mechanism in an electrically failed module using the argon ion milling, scanning electron microscopy (SEM), dual beam focused ion beam-SEM, scanning transmission electron microscopy energy dispersive x-ray spectroscopy, and time-of-flight secondary ion mass spectrometry is reported. It is found that the bond degradation is due to the galvanic corrosion in the Ag-Al bonding area. Specific attention is given to the information of microstructures, elements, and corrosive ions in the degraded bond. In this study, it is believed that the Ag-Al bond degradation is highly related to the packaging designs.

Abstract Aluminum-copper alloys are popular for many applications that take advantage of the combination of properties in the alloys. This paper describes the use of multiple advanced failure analysis tools to analyze the physical and chemical properties of Al-Cu alloy thin films.

Abstract Electrical resistance of M1/M3 stack for Aluminium based technology showed anomalous values when no Ti is inserted between AlCu and cap TiN. Process investigations lead to suspect formation of AlN layer at this interface. Blanket wafers were processed at different temperatures to reproduce the layer formation and characterize the film by numerous techniques including XPS and EELS-TEM profiling. Full use of the different results shows the formation of a very thin (a few nms) and highly resistive AlN layer at the cap TiN / AlCu interface as well as a thicker but less resistive AlN layer at the bottom TiN / AlCu interface. PVD process changes were attempted to reduce the M1/M3 button stack resistance. Modification of the N2/Ar flow ratio for TiN sputtering shows slightly more stoechiometric TiN with reduced stack resistance by 35%.

Abstract Experimental devices in a deteriorated state were encountered after 168 hours of inductive operating life stress, (IOL) testing. A metal grain boundary breakdown mechanism was found during the analysis of the device, which was creating a low resistance current path between terminals. The AlSiCu top metal was breaking down along the grain boundaries. In addition there was alloying of the Aluminum into the underlying silicon. This alloying was creating a short to the gate, source, and drain. Several variations in the metal stack, testing conditions, number, and dimensions of bond wires die size and mold compound were evaluated to better understand the cause of the inability to withstand IOL stress and to provide a process solution. The prevention of the AlSiCu front metal grain boundary breakdown during inductive life stress testing required a die size, bond wire dimension, and testing condition change to meet the performance specification. This change resulted in a reduced grain boundary breakdown and consequently prevented Al grain boundary breakdown, TiW barrier breakdown, and Al alloy spiking. The die change and modified testing conditions resulted in a successful pass through the IOL stress testing.

Abstract Autoclave Stress failures were encountered at the 96 hour read during transistor reliability testing. A unique metal corrosion mechanism was found during the failure analysis, which was creating a contamination path to the drain source junction, resulting in high Idss and Igss leakage. The Al(Si) top metal was oxidizing along the grain boundaries at a faster rate than at the surface. There was subsurface blistering of the Al(Si), along with the grain boundary corrosion. This blistering was creating a contamination path from the package to the Si surface. Several variations in the metal stack were evaluated to better understand the cause of the failures and to provide a process solution. The prevention of intergranular metal corrosion and subsurface blistering during autoclave testing required a materials change from Al(Si) to Al(Si)(Cu). This change resulted in a reduced corrosion rate and consequently prevented Si contamination due to blistering. The process change resulted in a successful pass through the autoclave testing.

Abstract In our previous paper [1], discolored bondpads due to galvanic corrosion were studied. The results showed that the galvanic corrosion occurred in 0.8 ìm wafer fabrication (fab) process with cold Al alloy (Al-Si, 0.8 wt%-Cu, 0.5 wt%) metallization. Galvanic corrosion is also known as a two-metal corrosion and it could be due to either wafer fab process or assembly process. Our initial suspicion was that it was due to a DI water problem during wafer sawing at assembly process. After that, we did further failure analysis and investigation work on galvanic corrosion of bondpads and further found that galvanic corrosion might be due to longer rinsing time of DI water during wafer sawing. The rinsing time of DI water is related to the cutting time of wafer sawing. Therefore, some experiments of wafer sawing process were done by using different sizes of wafer (1/8 of wafer, a quadrant of wafer and whole of wafer) and different sawing speed (feed-rate). The results showed that if the cutting time was longer than 25 minutes, galvanic corrosion occurred on bondpads. However, if the cutting time was shorter than 25 minutes, galvanic corrosion was eliminated. Based on the experimental results, it is concluded that in order to prevent galvanic corrosion of bondpads, it is necessary to select higher feed-rate during wafer sawing process at assembly houses. In this paper, we will report the details of failure analysis and simulation experimental results, including the solution to eliminate galvanic corrosion of bondpads during wafer sawing at assembly houses.

Abstract Discolored bondpads & non-stick failure in 0.6 μm wafer fab process with the hot Al alloy metallization was investigated. SEM, EDX & AES techniques were used to identify the root causes. Failure analysis results showed that discolored bondpads & non-stick failure were caused by TiN residue introduced during L95 bondpad opening wafer fab process. TiN residue on bondpad might have led to non-stick bondpad issue. The results also showed that it was difficult to determine the trace amount of TiN residue on bondpad using EDX technique due to its limitations. In this work, Auger surface analysis technique was used to determine TiN residue on bondpads with Al/TiW/Ti metallization. Auger results showed that Ti & N peaks were detected on discolored bondpads. It has resulted in non-stick bondpad failure. The solution to eliminate TiN residue on bondpads was to increase etch time at L95 bondpad opening wafer fab process. After using the new recipe with longer etch time, Auger results on the bondpads showed that no Ti & N peaks were detected and the bond-pull testing also passed.