Whisker Formation on SAC305 Soldered Assemblies

This article describes the results of a whisker formation study on SAC305 assemblies, evaluating the effects of lead-frame materials and cleanliness in different environments: low-stress simulated power cycling (50–85 (cid:2) C thermal cycling), thermal shock (–55 (cid:2) C to 85 (cid:2) C), and high temperature/high humidity (85 (cid:2) C/85% RH). Cleaned and contaminated small outline transistors, large leaded quad ﬂat packs (QFP), plastic leaded chip carrier packages, and solder balls with and without rare earth elements (REE) were soldered to custom designed test boards with Sn3Ag0.5Cu (SAC305) solder. After assembly, all the boards were cleaned, and half of them were recontaminated (1.56 l g/cm 2 Cl (cid:2) ). Whisker length, diameter, and density were measured. Detailed metallurgical analysis on components before assembly and on solder joints before and after testing was performed. It was found that whiskers grow from solder joint ﬁllets, where the thickness is less than 25 l m, unless REE was present. The inﬂuence of lead-frame and solder ball material, microstructure, cleanliness, and environment on whisker characteristics is discussed. This article provides detailed metallurgical observations and select whisker length data obtained during this multiyear testing program.


INTRODUCTION
After the European Union RoHS directive deadline was enacted in July 2006, the electronics industry began a transition to manufacturing with Sn-Ag-Cu (SAC) near-eutectic alloys to avoid the use of Pb-based solders. This change has had little impact on most commercial consumer products because of the limited life requirements and relatively benign use environments. However, lead-free implementation for the aerospace and defense industry requirements, which includes long service lifetimes, rugged operating environments, and high consequences of failure, requires additional evaluation to assure safe systems operation.
The new Pb-free and high Sn (about 96%) alloys may be susceptible to spontaneous growths of filament-like tin structures called tin whiskers. Pb is well known as an effective suppressant of whisker formation. Without Pb, the military, aerospace, and other high-reliability industries have experienced increased risks of system failure due to tin whiskers that cause electrical short circuits, impact highfrequency circuits, and create loose debris. 1,2 The majority of recent tin whisker research has concentrated on coupons or components with an emphasis on the Sn plating composition, thickness, grain size, grain orientations, and Ni underlayer. [2][3][4][5][6][7][8][9][10][11][12] These studies produced a great deal of knowledge; however, they do not consider the very real situation in which components are assembled on circuit boards using Pb-free solder pastes. Recent observations have demonstrated the ability of Pb-free solder joints to grow whiskers. 13,14 One challenge accompanying real electronic systems is the interplay among the component design and materials, manufacturing process, and service environments that contribute directly or conspire with one another to exacerbate whisker growth.
This article is focused on highlights from the Whisker Testing and Modeling project 15 funded by the U.S. Strategic Environmental Research Program. The objective of this project is to perform systematic tin whisker testing and Monte Carlo risk modeling on lead-free electronic assemblies in order to improve the reliability of military electronic systems. The observations described in this article are based on an extremely large set of data; 129724 whiskers were counted and 10985 whiskers were measured.

EXPERIMENTAL Approach
The experimental portion of this study was designed to study the role of selected manufacturing process variables in the growth of tin whiskers under certain isothermal and thermal cycling environments. The main assembly variables include package type and lead/ball materials as well as component and assembly cleanliness. Electronic components were attached to printed circuit boards to form a functional printed circuit assembly. Component leads were electrically and mechanically fixed to the board Cu pads with molten SAC305 solder. During reflow, the solder starts melting at 217°C. The solder then wicks up the leads and dissolves the electroplated Sn part. The rest of the electroplated Sn melts at 232°C and continues mixing with the molten phase. During cooling, this mixture solidifies. The temperature range of the solder joints across the board varies with the minimum acceptable temperature of 232°C and the maximum of 255°C. Therefore, after Pb-free reflow there is no original electroplated Sn coverage of the component leads. The modified component tin or tin alloy coverage after assembly might be thicker or thinner than electroplated Sn before assembly, and it has an elemental composition closer to the original SAC solder or pure Sn depending on the component type (length of the leads), location, and reflow parameter and solidified microstructure.

Test Vehicle
Three custom boards were designed to evaluate the key piece parts of interest. The small outline transistor (SOT) board has three, five, and six leaded SOT parts with C194 Cu alloy and alloy-42 alloy leads. The quad flat pack (QFP) board has C7025 Cu alloy high pin count QFPs with two lead pitches and a C151 Cu alloy plastic leaded chip carrier (PLCC). The ball grid array (BGA) board contains solder alloy balls that evaluate whisker growth on Ce rare earth element (REE) additions to SAC. The test vehicles for this study are small boards 6 cm 9 6 cm in size processed together 12-up on a panel (Fig. 1). The boards were separated after surface-mount soldering, inspected, and then subjected to the environments. The parts were distributed across three different board designs, designated as the SOT board, the QFP board, and the BGA board. The board was found to be well suited for inspection by scanning electron microscopy (SEM) because the board fit easily into the SEM's sample chamber. The placement area was limited to 5 cm 9 5 cm to ensure all leads of interest were contained in a region that could be viewed by the SEM. The boards are 0. 24  The SOT board has 64 alloy-42 lead material SOT3 Fairchild 2N7002 parts, 40 C194 lead material SOT5 Fairchild NC7S08M5X parts, and 17 alloy-42 lead material SOT6 Diodes Inc. 2N7002DW-7-F parts (Diodes Inc., Plano, TX). The lead composition for the alloy-42 is Fe-42Ni and the Cu alloy C194 is Cu2.1-2.6Fe-0.015-0.15P-0.05-0.2Zn. The QFP board has the following Cu alloy lead material (Practical Components Inc., Los Alamitos, CA) and Amkor Technology (Chandler, AZ) parts (Practical Components Inc.,): six C7025 lead material QFP44 A-QFP44-10 mm-0.8-3.2-DC-Sn (0.8-mm pitch) parts, four C151 lead material PLCC20 A-PLCC20T-DC-Sn (1.25-mm pitch) parts, and four C7025 lead material QFP64 A-LQFP64-0.7 mm-0.4 mm-2.0-DC-Sn (0.4-mm pitch) parts. The lead composition for the C7025 is Cu2.2-4.2Ni0.25-1.2Si0.05-0.3 Mg and for the C151 is Cu0.1Zr. Half of the SOT3, SOT5, QFP44, and QFP64 parts contained some leads with a 5-V bias and the remainder was grounded. The SOT6 and PLCC parts were not connected electrically and are contained in the zero volt bias data presented in this study.
The BGA board contains provisions for two types of BGA components (100 ball 0.8-mm pitch Amkor CABGA and a 97 ball 0.4-mm pitch Amkor CVBGA. In the present evaluation, BGA devices were not soldered to the boards because of the difficulty of inspecting for whiskers under the package; only balls were populated. Two different ball alloys were studied on the land pattern area SAC105 and SAC105 with Ce REE added. These were compared with pads printed with SAC305 paste.

Assembly
Before assembly components were divided into two groups. The first group was cleaned using the method developed in screening experiments. 16 The samples were cleaned twice to get the level of contamination 10 times below typical acceptable industry level and did not exceed 0.062 lg/cm 2 (0.4 lg/in 2 ) Cl. The second group was contaminated with NaCl using the method developed earlier. 16 The piece part level of chlorine contamination 0.465 lg/cm 2 (3 lg/in 2 ) was selected to be within the industry levels encountered (no standards exist).
Both component groups cleaned and intentionally contaminated were assembled using SAC305 solder paste. Assembled boards with clean and contaminated components were divided into two groups each. The first group was cleaned after assembly and the second group was purposely contaminated after assembly. The assembly level of equivalent chlorine contamination was selected to be within the J-STD-001 (IPC Association Connecting Electronics Industries, Bannockburn, IL) industry limits typically used to provide satisfactory electrical function-approximately 1.56 lg/cm 2 (10 lg/in 2 ) Cl. The contamination levels are designated as: 0-0 = no part contamination-no board contamination; 0-1 = no part contamination-board contamination; 1-0 = part contamination-no board contamination; and 1-1 = part contamination-board contamination.
For the assembly of the BGA boards, 0.4-mm (0.0157 in) diameter spheres were ordered from a major solder manufacturer. The target concentration was 0.5% Ce. The ball manufacturer had difficulty attaining this level and it was found to be<0.01% Ce. Then, after soldering to the board with SAC305 paste, the Ce concentration was further reduced.

Experimental Environments and Testing
Four environments were selected to assess whisker growth. There were two isothermal high humidity environments; a long-term low-temperature high humidity (LTHH) and a short-term hightemperature high humidity (HTHH). In addition, there were two thermal cycling conditions used: a simulated power cycling thermal cycle (PCTC) and a thermal shock cycle (TC). In high-humidity conditions, 85°C has been shown to promote whisker growth in lead-free solder alloys. [12][13][14] The two isothermal high-humidity environments employed were 25°C/85% RH (3 years) and 85°C/85% RH (4,000 h). The PCTC cycle was +50°C to 85°C with 15-min ramps and dwells in air simulating the conditions in Ref. 17 that grew whiskers when rework flux contamination was present. The TC cycle was -55°C to 85°C with three cycles per hour air-to-air thermal shock as defined in JESD201 Environmental Acceptance Requirements for Tin Whisker Susceptibility of Tin and Tin Alloy Surface Finishes (JEDEC Solid State Technology Association, Arlington, VA) and has representative temperature limits but temperature ramp rates that are much greater than moderate aerospace service conditions. Note that in the PCTC testing, the actual measured chamber temperature was 48-88°C and humidity was not controlled, but it was measured to be between 25%RH at 88°C to 10% RH at 48°C. For the TC cycle, the humidity was not controlled or measured.

Whisker Inspection
The assemblies were removed for inspection at progressively increasing exposure times. For example, the PCTC samples were first examined after 250 cycles, returned to cycling for an additional 500 cycles and inspected at 750 cycles (250 + 500), then returned for an additional 1000 cycles and inspected at 1750 cycles (250 + 500 + 1000). The industry whisker inspection and measurement standard JES-D22A121A Test Method for Measuring Whisker Growth on Tin and Tin Alloy Surface Finishes (JE-DEC Solid State Technology Association) developed for part-level whisker measurement was adapted for the assembled parts. The parts were randomly selected for inspection and approximately 50-100 leads were examined for each part condition. The same parts and leads were inspected by the same person for all environments to monitor the whisker growth progression on the leads and minimize operator related inspection variation. Inspections were performed at increasingly longer intervals with the boards being returned to the chamber. The whisker length criterion in JESD22A121A was used to perform the whisker length measurements in the SEM. Whiskers longer than 10 lm were measured for all experiments except for the HTHH 4000-h inspection, where only whisker lengths greater than approximately 30-40 lm were measured to concentrate limited inspection resources on the longest whiskers. A unique aspect of measuring whiskers on assemblies is that the whisker growth surfaces are nonplanar and the sample must be continually rotated and tilted during the inspection. In the current work, the reported whisker length measurements are conservative. During the length measurement procedure, the SEM inspection azimuth axis was adjusted to be aligned to within approximately 30°from perpendicular to the whisker. The SEM axis misalignment from the whisker normal results in a potential whisker length underreporting of up to 15%. All whisker lengths and diameters are reported in microns.
The detailed inspection was performed using an SEM. The occurrence of a whisker was counted if it was observable at 100 times magnification in the SEM. There was no differentiation between odd shaped eruptions and whiskers in the occurrence count. For the whisker-length measurements, an SEM magnification higher or lower than that used for inspection may be required, such that the whisker being measured approximately fills the field of view at the selected magnification. The numbers of whiskers were recorded along with the amount of surface area that was inspected as well as the region of the lead where the measurements were made. These were the same regions that were used to obtain the whisker length. For selected whiskers, the whisker diameter or thickness was measured by drawing a line perpendicular to the whisker axis. 12

Metallurgical Analysis
Sequential whisker cross sectioning was performed on representative whiskers with SEM inspection at various slice depths. A metallurgical evaluation was performed to determine the tin grain morphology, intermetallic (IMC) layer thickness and morphology, and IMC particle distribution at the base of the whisker and in the whisker itself. Optical and SEM images and EDX elemental spectrum were used to record findings similar to the results published by authors in 2008 and 2012. 16,17

Characterization of Components Before and After Assembly
SOT and QFP board parts were analyzed before assembly in the as-received condition, after cleaning and after intentional contamination. The assembled boards were cross sectioned to study the solder microstructure, component coverage, IMC characteristics, and contamination distribution.

As-Received Parts
There were no significant anomalies in the plating of the part leads relating to solderability. Some defects important for whiskering that are not commonly reported ( Fig. 2) such as exposed base metal, thin plating from lead forming, voids, roughness, and deep surface grooves and some ionic contamination such as Cl, S, Si, Na, and Br were detected. The QFP44, QFP64, and PLCC20 leads exhibited some instances of plating cracks. The SOT3 part was also noted to have some silicon contamination present before cleaning. The distribution of the contamination on the cleaned and re-contaminated part was distributed into the plating grooves and valleys similar to the part before cleaning. 16 Cross sectioning of the PLCC demonstrated that the Sn plating of the leads is extremely uneven. The XRF measurements reported Sn thicknesses of 8-10 lm; however, the actual thicknesses observed during cross sectioning varied from 1 to 38 lm. Because thin Sn plating is more prone to whisker growth, an 8-lm minimum tin plating thickness is recommended for whisker mitigation. 1

Assembly Characterization
After soldering, the solder coverage and IMCs were characterized using cross sectioning. A typical cross-section evaluation is shown in Fig. 3. The SOT3 and SOT6 and QFP64 leads were fully covered in solder, but the solder did not always extend to the top of the leads on the SOT5. The QFP44 and PLCC leads were partially covered with solder. The reflowed Sn lead finish beyond the solder no longer exhibited the fine-grain structure of the initial plating. The reflowed Sn and solder grain sizes were typically more than 25 lm. The thinnest IMC was observed on the alloy-42 leads (0.3 lm). With the alloy-42 leaded parts, the board (Cu, Ni) 6 Sn 5 IMC was thicker (2.6 lm) than the lead side intermetallic. The SOT3 part was found to have Cl trapped at the thinnest part of the solder joint between the lead and Cu pad.

Whisker Characterization After Environmental Testing
Highlights of the whisker length, growth location, and diameter are presented next. Currently the testing and data analysis are almost finished with the exception of the long term high humidity testing. The vast majority of measurement work was done on SOT boards because similar packages with different thermal coefficient of expansion (CTE) alloys were present. Table I summarizes the subset of whiskers counted and measured on the SOT boards.
The thermal cycling environments promoted whisker growth on the alloy-42 lead terminations, whereas the high-humidity environments caused greater whisker growth on Cu-leaded terminations. The results that follow are for leads that were either grounded or not connected. Preliminary inspection of powered devices indicated that bias did not have a significant impact on whisker growth, but the sample size was small.

PCTC
Whisker inspections were performed after 250, 750 (250 + 500), and 1750 (250 + 500 + 1000) cycles. No whiskers were observed at the 250 cycle inspection. At the 750 and 1750 cycle inspections, whisker nucleation and growth were observed (Fig. 4). The maximum whisker length was 19.4 lm on the SOT3 part with the 1-1 contamination level. Contamination level had a slight impact on whisker length and density. The whiskers grew in the region where the lead exits the solder fillet and the solder is thin (Fig. 5). Although the whiskers in this group were the shortest of all the experiments, it is believed that nucleation and growth would continue with more cycles as was observed in Ref. 17 .

TC
Whisker inspections were performed at 500 and 2110 (500 + 1610) cycles. The greatest whisker nucleation and growth occurred from the alloy-42 leads. During thermal cycling, the whisker growth is driven by the CTE differences between the low  CTE alloy-42 and the higher CTE solder. The longest whiskers were on the SOT6 termination; 32 lm after 500 cycles and 115 lm after 2,110 (500 + 1610) (Fig. 6). The whiskers on the alloy-42 lead terminations predominantly grew from regions where the solder was thin near the top of the main solder fillet; however, there were also massive tin eruptions indicating a significant amount nonwhisker stress relaxation (Fig. 7).

HTHH
Whisker inspections were performed at 1000 and 4000 (1000 + 3000) cycles. The HTHH environment yielded the longest whisker growth (Fig. 8) when compared with the PCTC and TC environments (note the 3-year LTHH is not yet complete). The HTHH assembly 1000-h exposure resulted in whisker lengths up to 186 lm, more than three times longer than the 45-lm JESD201 piece part test limit for 4000 h (55°C/85% RH). After 4000 h, the longest whisker was 214 lm on the SOT5 solder joints at the Cu board pad edge. While not part of the main measurement set, the QFP64 terminations also exhibited long tin whisker growth (Fig. 9). The intermediate contamination levels (0-1 and 1-0) exhibited the longest mean whisker length, but the 1-1 contamination grew the longest whiskers. The Cu-Cu (lead-pad) couple exhibited the greatest whisker nucleation and growth ( Table I). The alloy-42/Cu couple exhibited significantly less nucleation and growth after 1000 h than the Cu/Cu couple. However, as the exposure time increased, the whisker length difference was significantly reduced. During HTHH, the whisker growth is driven by oxidation and corrosion (discussed later). Although it is possible that additional contamination accumulated near the board, the cleaned assembly also exhibited significant whisker growth along the board pad edge. The majority of whiskers were between 1 lm and 5 lm in diameter regardless of alloy or contamination level. After 4000 h, the whisker density varied from 50 to 500 whiskers per termination across the lead material and contamination levels.
There was a marked difference in whisker growth location between the thermal cycling and HTHH. In PCTC, whisker growth was at the top of the solder fillet (Fig. 5) and in TC the whiskers grew from the thin solder on the lead, whereas during HTHH, the majority of whiskers grew from the thin solder regions on the Cu board pad edge (Fig. 10).

Recrystallization and Grain Change
The dynamic recrystallization theory proposed by Vianco and Rejent 18,19 suggests that there is an optimal stress for whisker growth, above which other nonwhisker growth stress relaxation mechanisms occur. In the current study, varying degrees of recrystallization and stress relaxation were observed. Recrystallized grains adjacent to whiskers have been observed after PCTC and TC (Fig. 11). In some cases, the recrystallization was below the surface (Fig. 12). Possible evidence of recrystallization and/or grain growth was found on the increasing or decreasing whisker diameters observed on the TC samples (Fig. 13). Note that whisker growth angle changes were also observed, which could be due to tin mass transport changes at the whisker base 20 or grain rotation during cycling. In contrast to observations by Susan et al., 20 sometimes substantial whisker growth occurred after the whisker base diameter increased. The reflowed SAC alloy generally has relatively large tin grains after reflow so recrystallization processes transforming large grains to small grains as part of whisker nucleation and growth are expected.

IMC
Primary IMCs such as Ag 3 Sn and Cu 6 Sn 5 particles promote whisker nucleation by increasing local stress in temperature cycling through differences in CTE, shear bands, and misoriented deformation zones around hard particles (Fig. 14). The growth of copper-tin IMC between the substrate and tin can also drive whisker growth. 3 During PCTC, the IMC on lead was observed to grow much faster than expected. The SOT3 IMC before cycling was 0.3 lm and after 1,750 PCTC cycles was 1.6 lm-more than a five times increase in thickness. In contrast, the IMC on boards before cycling was 2.6 lm and after cycling was 3.0 lm. In addition, large CuNiSn IMCs were observed in the solder fillets next to whiskers. It is postulated that enhanced Cu diffusion from the board pad to component during cycling promotes IMC formation that increases whisker growth. As will be discussed next, IMCs also contribute to oxidation and corrosion.

Oxidation/Corrosion
IMC particles contribute to uneven oxidation along the primary Sn grain boundaries, which creates local stress and promotes whisker formation (Fig. 15). The oxidation/corrosion often begins in the Sn interdentric spaces and can penetrate deeply into the solder. The solder fillet region was observed to be partially oxidized during the HTHH exposure with some oxide/corrosion regions traversing the entire solder fillet thickness to the substrate (Fig. 16). When all the tin around the whisker base becomes oxidized/corroded, whisker will stop growing. In addition, as oxidation/corrosion proceeds, whisker ductility is reduced and it is easier for the whiskers to become detached from the substrate. Corrosion was also observed adjacent to a whisker after the very low-humidity PCTC environment. The compressive stress caused by the 29-34% volume increase of the Sn oxides compared with the bSn promotes whisker growth. These findings are consistent with other investigators assessing the role of humidity on tin whisker growth on electronic component leads [21][22][23] and on lead-free assemblies. 5 It is important when studying whisker growth of solder joints that all the material interaction be considered. In alloy-42 solder joints, Cu 6 Sn 5 interfacial layer at the board pads and solder particles contain Ni, which reduces the galvanic potential between the IMCs and the Sn, slowing the oxidation rate and the accompanying whisker nucleation. Ni from alloy-42 retarded whisker nucleation from the board Cu pads (Fig. 17). This is due to the Ni in the alloy-42 promoting the formation of the (CuNi) 6 Sn 5 ternary IMC on the board Cu pad.
Surface roughness of the solder also contributes to corrosion-induced whiskering. The roughness is      partly a result of the shrinkage of the liquid between the primary tin dendrites. The roughness tends to trap contamination, which is difficult to clean (Fig. 12a).

Broken Whiskers
There are two possible explanations for the large amount of broken whiskers found during the   examination at 4000 HTHH hours. Some of the thin regions of solder were completely oxidized and had no whiskers on the surface (Fig. 16). This finding suggests that oxidation/corrosion propagating un-der a whisker can make the whisker attachment to the base more brittle. In another cross-section of a whisker through its base, voids and a crack were observed (Fig. 18).

Nonwhisker Growth Stress Relaxation
In some cases, nonwhisker growth stress relaxation occurred. During PCTC in the thicker solder region, faceted crystal growth was observed (Fig. 19). Under the higher stress conditions of TC, the alloy-42 solder joints eventually exhibited massive cracking (Fig. 20) and massive eruptions consisting of many recrystallized grains (Fig. 7).

Test Considerations
An important test observation was that the intermediate SEM inspections stopped some whiskers from further growth after resuming environmental exposure. This condition was most pronounced on the HTHH samples where the majority of whiskers inspected at 1000 h stopped growing further when inspected at 4000 h, but new whiskers formed (Fig. 21). The interruption of whisker growth by inspection during thermal   cycling (TC or PCTC) was less pronounced and existing whiskers continued to grow (Fig. 14). Thus, periodic inspection will cause an underreporting of whisker length. By progressively increasing time intervals or having longer uninterrupted tests, longer whisker growth would be obtained.

REE Oxidation
The SAC solder with REE was included in the test matrix because REE additions have increased the SAC solder whisker growth propensity. 24,25 Ce was chosen over La and Y because results have been published indicating that Ce has better oxidation resistance, 25 which would be promising for incorporation in lead-free solder. The preliminary experiment in the current work 26 had a different result; Ce was at least as effective as Y and La in whisker formation. Therefore, to discourage industry from even considering Ce additions to electronic solder, the BGA board used Ce at a concentration much lower than the 2% being considered for improving drop shock performance and whisker growth was still observed (Fig. 22). The manner in which RESn compound oxidation contributes to whisker growth is (I) liberation of Sn and (II) development of compressive stress by the RE oxide. Because REEs are less noble than Sn, RE in RESn 3 is more prone to oxidation, which results in  rapid oxidation of CeSn 3 (or YSn 3 and LaSn 3 ). In addition, the surface active nature of REEs results in a condition where RESn IMC tends to segregate to the surface giving it improved access to oxygen. RESn IMCs can also be exposed to air if cracks form during solder joint thermal cycling.

CONCLUSION
Based on a systematic study of electronic assemblies with leaded components covered with SAC305 solder, the following conclusions can be made. Whiskers grow from solder fillets around component leads and Cu pads, particularly where the solder is less than 25 lm thick. Very long whiskers can grow from SAC305 fillets. Whisker risks must be considered for high-reliability equipment. Thermal cycling promotes whisker growth when tin is on low CTE base materials. The stresses in the mild +50°C to +85°C PCTC cycle were sufficient to initiate recrystallization of the lead-free solder and nucleation of whiskers. Even though the À55°C to 85°C cycling does not create optimal stress conditions for whisker growth from alloy-42 terminations in SAC305 assembly, the alloy-42 leads still exhibited whisker lengths longer than the JESD201 piece part test limits. High humidity promotes whisker growth when thin SAC is on Cu. The 85°C/85 RH 1,000-h exposure on an assembly resulted in whisker lengths longer than the JESD201 piece part test limits for 4000 h. All the solder joint materials are important for ascertaining whisker growth. Although Ni tended to retard nucleation on Cu pads in HTHH, it tended to promote whisker growth by forming thick CuNiSn IMC on alloy-42 leads during PCTC. Assembly contamination is an important consideration for whisker growth in harsh service environments. REE additions to lead-free solder significantly increase whisker growth. Last, interruption of high-humidity conditions during interim inspections can cause an underreporting of whisker length.