International Journal of Aerospace Engineering

International Journal of Aerospace Engineering / 2012 / Article
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Condition-Based Maintenance

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Research Article | Open Access

Volume 2012 |Article ID 684024 |

Gino Rinaldi, Trisha Huber, Heather McIntosh, Les Lebrun, Heping Ding, John Weber, "Corrosion Sensor Development for Condition-Based Maintenance of Aircraft", International Journal of Aerospace Engineering, vol. 2012, Article ID 684024, 11 pages, 2012.

Corrosion Sensor Development for Condition-Based Maintenance of Aircraft

Academic Editor: Peter Foote
Received19 Feb 2012
Accepted10 Apr 2012
Published27 Jun 2012


Aircraft routinely operate in atmospheric environments that, over time, will impact their structural integrity. Material protection and selection schemes notwithstanding, recurrent exposure to chlorides, pollution, temperature gradients, and moisture provide the necessary electrochemical conditions for the development and profusion of corrosion in aircraft structures. For aircraft operators, this becomes an important safety matter as corrosion found in a given aircraft must be assumed to be present in all of that type of aircraft. This safety protocol and its associated unscheduled maintenance requirement drive up the operational costs of the fleet and limit the availability of the aircraft. Hence, there is an opportunity at present for developing novel sensing technologies and schemes to aid in shifting time-based maintenance schedules towards condition-based maintenance procedures. In this work, part of the ongoing development of a multiparameter integrated corrosion sensor is presented. It consists of carbon nanotube/polyaniline polymer sensors and commercial-off-the-shelf sensors. It is being developed primarily for monitoring environmental and material factors for the purpose of providing a means to more accurately assess the structural integrity of aerospace aluminium alloys through fusion of multiparameter sensor data. Preliminary experimental test results are presented for chloride ion concentration, hydrogen gas evolution, humidity variations, and material degradation.

1. Introduction

Metals are vulnerable to corrosion due to environmental factors, and in the majority of cases engineering-grade metals and alloys are selected based on design and functionality priorities: strength, light-weight, mechanical and electrical properties, and so forth, rather than corrosion resistance per se [1]. Unfortunately, the cost of corrosion has a substantial impact on the economies of all nations with the United States spending approximately $437 billion annually for corroded infrastructure maintenance and replacement [2].

This costing trend is increasing because aircraft are exposed to service operating environments that negatively impact their long-term durability. This is an on-going design, materials selection, and maintenance scheduling issue whose combined neglect or oversight can lead to a shortened life cycle or catastrophic failure of the aircraft [3, 4]. For aircraft, the effects of corrosion damage are cumulative and can increase in severity if the damage is not detected early. A serious result of undetected corrosion is that it can have a cascading effect by which it can precipitate and accelerate fatigue damage [5] leading to a corresponding decrease in the load bearing capacity for that structure. In this respect, the structural integrity of the aircraft is undermined by two separate yet complicit factors. Corrosion damage occurs slowly, insidiously, and often out of sight. In the short term, it may represent only a small part of the total maintenance cost of a short-life aircraft; however, due to its cumulative nature, corrosion damage-based maintenance expenses will inflate to a substantial amount the ownership cost of a long-life aircraft at retirement [6].

Due to the extreme environments often encountered in military and search-and-rescue (SAR) air operations, these types of aircraft are often flown in conditions that can be considered to be “pushing their design and operational limits.” As an example, exposure of a few hours to sea water may cause pitting, and if it is not removed, as can happen in hidden or difficult to access areas, it can lead to premature crack nucleation in aircraft components [7]. Also, dissolved chlorides are known to be involved in the penetration of the protective aluminium oxide layer [8]. The combined effects of corrosion and accelerated fatigue due to corrosion will eventually limit the performance and availability of these aircraft. Presented in Figure 1 are images of Canadian Forces and SAR aircraft [9] in various typical operational modes.

The integrated corrosion sensor development program presented here intends to mitigate these consequences by providing a condition-based approach to aircraft maintenance protocols through a data-intensive maintenance scheduling methodology. The primary aim is to trim maintenance schedules down to actual structural, component or material requirements as opposed to operating under predefined inspection timetables. Presented in Figure 2 is a schematic of various factors involved in the corrosion process. Using data fusion, these factors will determine a corrosion index, which in turn will determine the condition-based maintenance (CBM) protocol. Figure 3 shows a proposed breakdown of the CBM into preventative and corrective protocols as a function of the corrosion index.

2. Aluminium Corrosion Chemistry in Aqueous Solution

2.1. Aluminium Oxide Passivation Layer

Aluminium is only workable from an engineering point of view because of the existence of a natural aluminium oxide (Al2O3) protective layer, without which it would react violently. Aluminium reacts quickly with any available oxygen source to immediately form Al2O3. This thin layer inhibits chemical interaction between bare aluminium and the local environment. However, aqueous solutions carrying anionic species can diffuse through Al2O3 and lead to corrosion [10]. The corrosion process of aluminium (Al) in aqueous solutions involves a combination of several factors: (i) moisture; (ii) anionic concentration (chloride); (iii) pH of the solution; (iv) temperature [11, 12].

The protective reactions, in air and water, respectively, are given as

Equation (2) indicates that the reaction of Al with water (H2O) will also release hydrogen gas (H2).

2.2. Oxidation Reduction

The oxidation reaction of Al (in H2O) is given by [13]:

Trivalent Al ions () readily bind with chloride () and hydroxide () ions present in the solution, and this bonding competition either leads to continued degradation of the layer or its regeneration, respectively.

The above reaction is electrochemically balanced by a corresponding reduction reaction given by [13]: where the hydronium () ions are a result of the dissolution of given by

Generally, the dissolution of Al in water is the sum of the oxidation and reduction reactions, as given by (3) and (4):

Employing (5) and (6), the dissolution of Al with water results in the formation of aluminium-hydroxide () and the release of H2 and is given by [8, 14, 15]:

2.3. Chloride-Based Aqueous Solution

Chloride enters the aqueous solution through the absorption of gaseous hydrochloric acid or an organic gas containing chlorine or through the deposition of sea salt [16]. For chloride-based solutions, the oxidation/reduction reactions would involve the following [17]:

As more and more is adsorbed, repair of the layer is no longer possible, and corrosion proceeds rapidly [12, 18]. This process is shown schematically in Figure 4(a). Competitive adsorption of , or at lattice sites will result in either continued dissolution or reoxidization, respectively [1820]. A sample chain structure for a dissolution complex is shown in Figure 4(b) (adapted from [21]).

2.4. Hydrochloric Acid

Hydrochloric acid represents an aggressive environment for Al, particularly Al alloys [13, 16, 22]. After penetration by , the dissolution process continues as follows: where HCl further attacks the layer: which exposes more bare aluminium to HCl and the evolution of [23]:

When fully corroded, 1 gram of Al will produce 1.245 litres of H2 gas [23]. The AlCl3 in (9) can then further react with H2O to create more HCl (as in (11)), and the dissolution process continues. Of importance, during the corrosion process, gas creates blisters on the Al surface due to gas accumulating in microcavities beneath the layer, thereby causing structural damage [24].

3. Sensor Node Development

3.1. Hydrogen Gas and Humidity Sensing Nodes: Conducting Polymer-Based Sensing

Conducting polymers become electrically conductive through the addition or removal of -electrons; however, polyaniline [25] (PANI) is more commonly doped by the addition of an acid. Shown in Figures 5(a) and 5(b) is a sample acid-doped chemical structure of PANI [26, 27]. The electrical conductivity of PANI depends on the size and shape of the acid anion [27], and it may be further enhanced by incorporating carbon nanotubes (CNTs) in the preparation of the polymer [28]. The addition of carbon nanotubes is thought to influence the semiconductor charge carrier mechanism (p-doped or n-doped) in polyaniline. Carbon nanotubes also significantly increase the current output of I-V type tests [29] because CNTs exhibit greater electrical conductivity along their length as compared to conducting polymers, although bulk CNTs do not conduct as well as expected, as the charge transfer is believed to occur by hopping. The conductivity of composites apparently exceeds that of the parent materials alone. This apparent synergy is attributable to the reduction in contact resistance between CNTs by the presence of the conducting polymer. The PANI/CNTs blend can then be readily applied to a sensing platform such as interdigitated electrodes (IDEs). Shown in Figure 6 is a schematic of an IDEs chip coated with PANI/CNTs (not to scale).

3.2. Integrated Chloride Ion, Relative Humidity, and Temperature Sensing Node

The development of this node presents an opportunity for integrating various “corrosion” sensors within the same enclosure. Also, the electronics and the associated computer interface capability being developed in parallel will provide a means that can allow for simultaneous data acquisition from the various sensors. At this stage of the corrosion sensor project, it can be considered as a prototype from which refinements in sensor integration, electronics and scaling-down can be developed. This unit consists of COTS chloride ion, relative humidity, and temperature sensors. Currently, the primary components include (i) a chloride ion electrode (Cole-Parmer Instrument Company); (ii) an ion concentration controller that interfaces to the electrode (B&C Electronics IC 7685); (iii) a packaged SHT21 humidity and temperature sensor (Sensirion AG); (iv) an MSP430FG461x/F20xx Experimenter’s Board (Texas Instruments). Presented in Figure 7 is an overview of the integrated sensor. The microcontroller communicates with the SHT21 sensor through an I2C bus and reads the chloride ion level detected by the IC 7685 controller through one of its analog inputs (ADC0). The microcontroller platform is MSP430FG4618 (Texas Instruments). The firmware resides in the FLASH memory of the microcontroller device and performs various functions required for detection of chloride ion, temperature, and relative humidity. On power up, the system boots automatically and enters the default mode for detection.

At the current developmental stage of the corrosion sensor project, the microcontroller hardware and firmware are very much underutilized. For example, only one of the eleven available analog inputs is used, and the firmware is often in “sleep” mode. Thus, such a microcontroller system has room to accommodate future extensions such as adding more sensing elements, and more functions. In this respect, the integration of additional features along with size and weight reductions forms the basis for the next phase of the project.

3.3. Material Degradation Sensing Node

For the material degradation sensing node, an XCorr multiarray sensor (Aginova Inc.) was adopted. This sensor is a 16-element passive electrochemical sensor that does not require any applied voltage for operation (Figure 8(a)). The sensor’s 16 elements are designed to measure uniform or localized corrosion through a naturally occurring corrosion-current between anodic and cathodic sites on the metal surface when it is exposed to a corrosive solution. The probe’s 16 elements are connected together through a common interface within the electronics (Figure 8(b)). The corrosive aqueous solution creates both cathodic and anodic sites at the elements on the probe head (Figure 8(c)). In this regard, corrosion at anodic sites can develop as on an actual metal surface. The system integrates data from the 16 individual elements and extrapolates both average and maximum yearly corrosion rates (Faraday’s Law).

4. Experimental Section

4.1. Polyaniline Preparations

In its finished form, PANI/CNTs blends resemble a dark powder, as shown in Figure 9(a). In this state, it cannot be employed directly for sensing applications but must be dispersed in a suitable solvent in order to apply it to a sensor surface such as IDEs. In this work, two types of metallic IDEs (Synkera Technologies Inc.), platinum (Figure 9(b)) and gold (Figure 9(c)), were employed for hydrogen gas and humidity sensing, respectively. Figure 9(d) shows a platinum  mm2 IDEs chip coated with a PANI/CNTs blend. In this figure, the IDEs chip is mounted onto a small electrical bread-board for ease of wiring and handling.

4.1.1. PANI: Hydrogen Gas Sensor Node

Hydrogen sensing using PANI and PANI/CNTs blends has been reported in the literature [3032]. In this work, camphor sulfonic acid (CSA) was employed as the doping material. The PANI/CSA/CNTs were dispersed in a chloroform solvent (0.040 grams PANI/CNTs powder per mL solvent). The mixture was then placed into a sonication bath for approximately 18 hours in order to obtain a uniform suspension. Small pipettes were used to transfer the solutions, and drop small amounts onto platinum IDEs. Spin-coating (2000 RPM for 1 minute) was used to distribute the solution over the IDEs surface.

4.1.2. PANI: Humidity Sensor Node

Humidity sensing using PANI blends has been reported in the literature [3335]. In this work, the PANI humidity sensitization was prepared by doping PANI with bis-(2-ethylhexyl) phosphoric acid (HDEHP), toluene, and CNTs. For this preparation, ethanol was employed as a dispersing solvent (0.021 grams PANI/CNTs powder/0.5 mL solvent). The same transfer, sonication, and spin-coating procedures, as described previously, were employed. For humidity sensing, a gold IDEs chip was used.

4.1.3. Electrical Continuity Measurements

The electrical continuity of the deposited polymer was measured by applying a ramp voltage (0–500 mV) across the polymer-coated IDEs and measuring the resulting current. A sample result is shown in Figure 10(a). The equation relating resistance (), length (), cross-sectional area (), and resistivity () of an electrical conductor is given as

Due to the nature of the spin-coating polymer deposition process, and can vary between sensors. A sample conductivity curve is shown in Figure 10(b).

Given in Table 1 are the electrical continuity characteristics for the various IDEs/polymer sensors tested. The resistances shown include the contact resistance of the pads, associated wiring, and the particular PANI formulation. For ease of comparison, in this table the conductivity100 is a derived value for a polymer thickness of 100 microns.

Sensor designationsResistance (S/m)


4.2. Experimental Results
4.2.1. PANI/CSA Hydrogen Sensing

The PANI/CSA-based sensors developed for hydrogen sensing were tested in a dry hydrogen/argon atmosphere. Presented in Figure 11 is an overview of the fully automated gas flow system and electrical interface. Data was acquired in real time and transferred to a PC (not shown). Shown in Figure 12 is a typical response obtained for the hydrogen sensors. It can be seen from this figure that the PANI/CSA formulation is sensitive to the presence of hydrogen. However, it is summarized that the similar responses seen for different hydrogen concentrations are in part due to hydrogen-bonding sites within the PANI/CSA material not being fully vacated when the flow is stopped or it is possible that the saturation point for this particular PANI/CSA formulation is below 1% hydrogen. Another possibility is that despite curing of the polymer in a dessicator prior to testing, some residual moisture may have remained trapped, thereby limiting the effective sensitivity of the PANI/CSA in these tests.

4.2.2. COTS Hydrogen Sensor

Described here is an experiment in which hydrogen gas was detected evolving from 6061-T6 aluminium alloy in a 5% saltwater solution. This test was carried out to demonstrate the possibility of measuring hydrogen evolution for corrosion monitoring of aluminium. Testing was carried out with a COTS hydrogen sensor (Kebaili Corporation) as shown in Figure 13(a). This sensor is capable of measuring hydrogen up to 4% per volume in air and is based on the microcatalytic oxidation of hydrogen. The variation of the sensing element resistance due to the exothermic reaction of hydrogen oxidation is directly proportional to the hydrogen concentration. In these tests, the baseline offset of the sensor was set to 215 mV. These “accelerated” corrosion tests consisted of immersing 6061-T6 aluminium alloy shards (Figure 13(b)) into a 5% salt water solution. The hydrogen sensor was affixed inside a 250 mL glass jar and then placed over a small opening in the plastic cover (Figure 13(c)). The glass/plastic interface was sealed with a putty material. The aluminium was left in the saltwater solution for ~36 hours prior to testing. A digitized acquisition system (Omega instruNet) was employed for the data acquisition. The result, shown in Figure 13(d), shows a gradual increase in the hydrogen concentration over time. In this figure, the sensor output increased by 15 mV over the measuring span, which corresponds to ~3% hydrogen (7.5 mL) within the glass container, which in turn indicates that approximately 6 mg of aluminium was consumed.

For aircraft applications, hydrogen sensing would require an enclosed area, where the diffusion of hydrogen is reduced and the gas concentrations reach levels that are practical for detection. Enclosed fuel storage areas such as under-fuel bladders, where condensation can form and initiate corrosion, are seen as potential areas for monitoring hydrogen gas evolution.

4.2.3. Humidity Sensor Node

Humidity sensor tests were conducted using a small container that allowed the flow of humid air through it. Both a PANI/HDEHP + toluene formulation IDEs sensor and a COTS (Omega RH820) sensor were placed inside the container for humidity sensing. Presented in Figure 14 is a comparison between the humidity sensitive response of the PANI-based and the COTS sensor as a function of time. As can be seen, the PANI sensor responds very well to humidity with excellent response.

4.2.4. Chloride Ion and Material Degradation Sensor Nodes

The chloride ion and material degradation testing was carried out in a salt-fog chamber (Singleton Corporation) as shown in Figure 15(a). The chloride ion sensor and material degradation sensor were placed into a beaker of deionized water (Figure 15(b)). Salt-fog condensate (3.5% sodium chloride solution) was captured within the beaker and mixed with the deionized water. Data was acquired over a two-hour span. Shown in Figure 16 is a comparison of the increase in chloride concentration and material degradation as a function of time.

Shown in Figure 17 is the dependence of the yearly corrosion rate on chloride ion concentration (40–130 ppm range).

From Figures 16 and 17, it can clearly be seen that salt-fog condensation into the prepared beaker containing deionized is detected by the increase of concentration and also in the increase in the corrosion rate of test metal electrodes. For example, a concentration of ~90 ppm corresponds to a corrosion rate of 900 microns/year. Hence, if such a solution were to remain undetected for an extended period of time, it could cause significant damage to an aircraft structure.

With the cumulative data of the various sensors, it will be possible to cross-correlate the influence of each corrosion parameter. In this way a theoretical corrosion index can be developed. In this regard, further testing is required in order to obtain adequate data for a more in-depth analysis and interpretation. This being said, the corrosion index will provide an indication of the environmental and material conditions so that either preventative or corrective maintenance actions can be taken.

At this stage the sensors are still in the developmental stage. However, as further refinement to the sensing technology is conducted, it is the aim that their use in aircraft will be in areas most prone to corrosion such as the cockpit in fighter aircraft, galley and latrine areas, or any other area prone to the accumulation and retention of moisture.

5. Conclusions

Part of the ongoing development of a multiparameter integrated corrosion sensor, consisting of carbon nanotube/polyaniline-based and commercial-off-the-shelf sensors, has been presented. This paper also described the integration methodology being investigated for the various sensor nodes and presented preliminary chloride ion, humidity, and temperature data acquisition capabilities. Also, experimental test results were presented for chloride ion concentration, hydrogen gas evolution, humidity variations, and material degradation. The integrated corrosion sensor development program presented here intends to provide a condition-based approach to aircraft maintenance protocols through a data-intensive maintenance scheduling methodology in order to tailor maintenance schedules for structural/component/material requirements as opposed to operating under predefined inspection timetables. Through data fusion, environmental and material factors were proposed for determining a corrosion index, which in turn was suggested for developing condition-based maintenance protocol consisting of both preventative and corrective maintenance scheduling.


The technical support given by Dr. Gerardo Diaz-Quijada and Dr. Bhavana Deore from NRC Steacie Institute for Molecular Sciences, and Dr. Jim Tunney and Dr. Jeffrey Dunford from NRC Institute for Chemical Process and Environmental Technology is gratefully acknowledged.


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Copyright © 2012 Gino Rinaldi et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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