Citation:) The Fitness Cost of Fluoride Resistance for Different Streptococcus mutans Strains in Biofilms. The Fitness Cost of Fluoride Resistance for Different Streptococcus mutans Strains in Biofilms
published: 28 August 2017 Published: 28 August 2017 (2017

Charles W Knapp
Sandeep Sharma
Xi Wei email@example.com
Dong Mei Deng firstname.lastname@example.com
Y Cai
Y Liao
Brandt Bw
Wei X
Liu H
Crielaard W
Van Loveren
C
Deng Dm
Yanling Cai
Department of Operative Dentistry and Endodontics
Guanghua School of Stomatology, Hospital of Stomatology
Sun Yat-sen University
GuangzhouChina

Guangdong Province Key Laboratory of Stomatology
GuangzhouChina

Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

Ying Liao
Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

Hospital of Stomatology
State Key Laboratory of Oral Diseases
Sichuan University
ChengduWest ChinaChina

Bernd W Brandt
Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

Xi Wei
Department of Operative Dentistry and Endodontics
Guanghua School of Stomatology, Hospital of Stomatology
Sun Yat-sen University
GuangzhouChina

Guangdong Province Key Laboratory of Stomatology
GuangzhouChina

Hongyan Liu
Department of Operative Dentistry and Endodontics
Guanghua School of Stomatology, Hospital of Stomatology
Sun Yat-sen University
GuangzhouChina

Guangdong Province Key Laboratory of Stomatology
GuangzhouChina

Wim Crielaard
Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

CorVan Loveren
Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

Dong Mei Deng
Guangdong Province Key Laboratory of Stomatology
GuangzhouChina

Department of Preventive Dentistry
Academic Centre for Dentistry Amsterdam
University of Amsterdam and Vrije Universiteit Amsterdam
AmsterdamNetherlands

University of Pennsylvania and Thomas Jefferson University, United States Rodolfo García-Contreras
University of Strathclyde
United Kingdom

National Autonomous University of Mexico
Mexico

Citation:) The Fitness Cost of Fluoride Resistance for Different Streptococcus mutans Strains in Biofilms. The Fitness Cost of Fluoride Resistance for Different Streptococcus mutans Strains in Biofilms
81630published: 28 August 2017 Published: 28 August 2017 (201710.3389/fmicb.2017.01630Specialty section: This article was submitted to Antimicrobials, Resistance and Chemotherapy, a section of the journal Frontiers in Microbiology Received: 07 June 2017 Accepted: 11 August 2017ORIGINAL RESEARCH Edited by: Reviewed by: *Correspondence:Streptococcus mutansfluoride resistancechlorhexidinelow pHsodium fluoridefitness costbiofilm
The cariogenic bacterium Streptococcus mutans can develop stable resistance to fluoride through chromosomal mutations in vitro. Fluoride-resistant S. mutans has seldom been isolated in clinical settings, despite the wide application of fluoride in oralcare products. One explanation is that the fluoride-resistant S. mutans strains have decreased fitness. However, so far, there has been no conclusive evidence to support this idea. The aim of this study was to investigate the fitness cost of 48-h biofilms of two fluoride-resistant S. mutans strains, UF35 and UA159-FR (UAFR), using the wild-type fluoride-sensitive strain UA159 as a reference. The engineered UF35 strain contains one point mutation, whereas UAFR, selected from NaF-containing agar plates, has multiple chromosomal mutations. All biofilms were formed for 48 h under a constantly neutral pH or a pH-cycling (8 h of neutral pH and 16 h of pH 5.5) condition in the absence of fluoride. The biomass of the biofilms was quantified with a crystal violet assay. The biofilms were also treated with chlorhexidine or solutions at pH 3.0, after which their lactic acid production was quantified. Compared to the UF35 and UA159 biofilms, the biomass of UAFR biofilms was two-four fold higher, and the UAFR biofilms were more resistant to chlorhexidine and low pH in terms of lactic acid production. No difference in biomass and lactic acid production was detected between UF35 and UA159 biofilms. The fluoride resistance of UAFR and UF35 strains in biofilms was further confirmed by treating the biofilms with NaF solutions. The level of NaF resistance of the three biofilms is generally ranked as follows: UAFR > UF35 > UA159. In conclusion, there is indeed a fitness consequence in UAFR, but surprisingly, this fluoride-resistant strain performs better than UF35 and UA159 under the described conditions. In addition, UF35 did not display a reduced fitness; it performed as well as the wild-type fluoride-sensitive strain.

INTRODUCTION

Fluoride is the most effective caries-preventive agent. Since the 1940s, it has been added to water supplies and to daily oral care products, such as toothpaste, mouthwash, and dental floss (Birkeland and Torell, 1978). It not only protects dental hard tissues by inhibiting demineralization and enhancing remineralization but also functions as an antimicrobial agent (Van Loveren, 2001;Ten Cate, 2004). Fluoride is able to suppress bacterial growth and metabolism Van Loveren et al., 1991b). To counteract this suppression, several oral bacterial species, including Streptococcus mutans, have acquired resistance to fluoride in the presence of a high fluoride concentration (Hamilton, 1969;Streckfuss et al., 1980;Bunick and Kashket, 1981;Sheng and Liu, 2000).

Streptococcus mutans has been recognized as one of the major cariogenic microorganisms because it can produce a large amount of lactic acid when given sugar; it is able to tolerate a low pH and it strongly forms biofilms in the presence of sucrose (Loesche, 1986). In a laboratory setting, several fluorideresistant S. mutans strains have been isolated under high fluoride concentration conditions. These strains were able to grow at fluoride concentrations at least three times higher than the concentration optimal for fluoride-sensitive S. mutans strains. This acquired fluoride resistance is rather stable as it persisted for at least 50 generations when cultivated without fluoride. We previously identified multiple single nucleotide mutations in the genome of a fluoride-resistant S. mutans strain (Liao et al., 2015), indicating that the stable resistance to fluoride was the result of genetic mutations.

Interestingly, the stable fluoride-resistant S. mutans strains have only been obtained in a laboratory setting so far. There has been no report of a resistant strain in clinical samples (Liao et al., 2017). This is surprising because fluoride-containing products have been widely applied in daily life. One explanation was that the microbes lost their fitness once they became fluoride resistant. It is known that the antimicrobial-resistant microbes could suffer a decrease in biological fitness (Andersson and Hughes, 2010). These fitness costs made antimicrobial-resistant microbes less competitive than susceptible strains when the selective pressure from antimicrobials was removed, which might eventually result in the loss of the antimicrobial resistance (Andersson and Hughes, 2010). In order to understand the effect of fluoride resistance on bacterial fitness, several laboratoryderived fluoride-resistant S. mutans strains were compared to their isogenic wild-type strains on growth, acidogenicity, and surface adherence in vitro or in animal models (Rosen et al., 1978;Lau and Kral, 1987;Van Loveren et al., 1991a;Liao et al., 2015). However, the results from these studies were inconsistent. For example, the fluoride-resistant S. mutans strain C180-2FR, was reported to be less acidogenic than its parent strain in one study (Van Loveren et al., 1991b), but found equally acidogenic to the same parent strain in another study (Liao et al., 2015). Van Loveren et al. (1991a) studied the competition between C180-2FR and its parent strain C180-2 in a rat model. The fluoride-resistant C180-FR strain colonized less and was eventually outgrown by its parent strain. However, Hoelscher and Hudson (1996) characterized another fluorideresistant S. mutans isolate (NCH105) and reported that this strain adhered to the tooth surface to the same extent as the parent strain (UA130). Differences in experimental design or different strains used in these studies may be the reasons for these discrepancies. As a result, it is hard to draw definitive conclusions about the fitness costs of fluoride resistance.

The aim of this study was to investigate the fitness of two fluoride-resistant S. mutans strains (UAFR and UF35) in biofilms, using the isogenic wild-type stain UA159 as a reference. The fluoride-resistant strain UAFR was created by culturing UA on agar plates containing increasing concentrations of fluoride (Zhu et al., 2012), whereas strain UF35 was engineered by changing a single nucleotide (-44A→C) in the promoter region mutp of UA159 (Liao et al., 2016). Both strains displayed a slower growth rate than the wild-type strain in suspensions. S. mutans biofilms rather than planktonic cultures were examined, because biofilms better mimic the bacterial life-style in dental plaque. Moreover, various bacterial growth environments in an oral cavity were simulated by growing bacterial cells under either a constantly neutral pH or pH-cycling conditions. The pH-cycling consists of a period of 8 h at neutral pH and a period of 16 h at pH 5.5.

MATERIALS AND METHODS

Bacterial Strains and Growth Conditions

The strains used in this study were the fluoride-sensitive S. mutans strain UA159 and two fluoride-resistant strains (UF35 and UAFR). The construction of strain UF35 was described in Liao et al. (2016). The strain UAFR (accession: NZ_CP007016.1) was kindly provided by Professor Zhimin Zhang (Jilin University, Changchun, China). All strains were routinely maintained on Brain-Heart Infusion (BHI) agar in a jar filled with anaerobic gas (80% N 2 , 10% CO 2 , and 10% H 2 ) at 37 • C. The medium for biofilm formation was a semi-defined biofilm medium (BM) (Deng et al., 2009). The pH of BM was adjusted either to 7.0 by adding 76 mM K 2 HPO 4 and 15 mM KH 2 PO 4 , or to 5.5 by adding 100 mM acetic acid. The specific pH used during biofilm formation is explained in detail below. BM with 0.4% glucose (BMG) or 0.2% sucrose (BMS) was used as a medium for the growth of pre-cultures and biofilm formation, respectively.

Biofilm Formation

Biofilms were formed in an active attachment model to avoid bacterial sedimentation (Li et al., 2014). This model consists of a standard 96-well microtiter plate and a lid with 96 polystyrene pegs that fit into the wells (Nunc TM , Roskilde, Denmark). Overnight (16 h) cultures of S. mutans UA159, UF35, and UAFR in BMG were adjusted to a final OD 600 of 0.035 in fresh BMS (pH 7.0). The optical density at 600 nm was used to measure bacterial growth of the overnight cultures only. Two hundred microliters of each culture was dispensed into each well of the microtiter plates. The lid with the pegs was then placed over the wells. The plates were incubated anaerobically. After 8 h, half of the biofilms, which formed on the pegs, were transferred to wells containing BMS at pH 7.0, whereas the other half were transferred to BMS at pH 5.5. The biofilms were further incubated for 16 h. Then the biofilms were transferred to wells containing BMS at pH 7.0 for another 8 h. Part of these 32-h biofilms were exposed to NaF. The others were transferred to either BMS at pH 7.0 or BMS at pH 5.5 for an additional 16 h. These 48-h biofilms that were not exposed to NaF were challenged by either chlorhexidine (CHX) or low pH. The schema of biofilm formation and biofilm processing is illustrated in Figure 1. All experiments were repeated three times. For each test condition, four replicates were used in every experiment.

Sodium Fluoride (NaF) Treatment

An initial experiment was carried out in our laboratory to determine the appropriate duration for the NaF treatment. The results indicated that the biofilms displayed detectable phenotypic changes after incubation with NaF for 16 h (data not shown). Therefore, NaF was added to the growth medium at 32 h and its effects on biofilm formation and lactic acid production was subsequently examined after 16 h of incubation. In detail, the 32-h biofilms were incubated in BMS containing various concentrations of NaF (0-12.5 mM) for 16 h. The pH of the BMS was 7.0 for the biofilms formed in constantly neutral pH and 5.5 for the biofilms formed in the pH-cycling condition. The biofilm formation in NaF-medium over 16 h was quantified by a crystal violet assay. The capability of the 48-h biofilms to produce lactic acid was also tested.

Chlorhexidine (CHX) Treatment

The 48-h biofilms that were not exposed to the NaF (see Figure 1) were inserted into wells containing 200 µL CHX solutions at concentrations of 0, 0.01, 0.02, and 0.04% for 5 min. The CHX solutions were prepared from a 20% chlorhexidine digluconate solution (Sigma-Aldrich, St. Louis, MO, United States). The treatment was stopped by inserting the biofilms into a neutralizing solution (6% Tween 80, 0.6% lecithin, and 0.068% potassium phosphate, pH 7.0) for 10 min (Kara et al., 2006). Thereafter, the capability of the biofilms to produce lactic acid was evaluated.

Low-pH Challenge

The 48-h biofilms that were not exposed to the NaF treatment (see Figure 1) were rinsed with sterile distilled water and then inserted into wells containing an acid solution at pH 3.0. The acid solution was prepared from 40 mM potassium phosphate/citrate buffer (Svensater et al., 1997). The duration of the treatment varied depending on the conditions of biofilm formation. The biofilms formed in the constantly neutral pH condition were treated for 1, 3, and 5 min, whereas the biofilms formed in the pH-cycling conditions were treated for 5, 10, and 30 min. The treatment was terminated by inserting the biofilms into a 300 mM HEPES [4-(2hydroxyethyl) piperazine-1-ethanesulfonic acid] buffer solution (pH 7.0) for 10 min. The lactic acid production of the biofilm was evaluated directly after the treatment.

Crystal Violet Staining Assay

A crystal violet staining assay (Li et al., 2014) was used to quantify the biomass of the biofilms with or without NaF treatment. The pegs with biofilms were first inserted into a 0.01% crystal violet solution (200 µL/well) for 5 min, washed twice with distilled water, and then inserted into 2% sodium deoxycholate to destain for 5 min. The absorbance of the used destaining solution was measured at 608 nm using a spectrophotometer (Spectramax Plus, Molecular Device, Sunnyvale, CA, United States). The change in biomass during the 16-h overnight incubation was calculated as: the OD 608 of 48-h biofilms minus the OD 608 of 32-h biofilms. The data are presented as the percentage of biofilm formation in a NaF group relative to that in the corresponding non-NaF treated control group.

Lactic Acid Quantification

To quantify the capability of the biofilms to produce lactic acid, the pegs with biofilms were incubated in an assay buffer containing 1% glucose (200 µL/well) for 1 h at 37 • C. The assay buffer was prepared from BM without yeast extract to avoid bacterial growth during the 1-h incubation (pH 7.0). The lactic acid concentration in the buffer solution was quantified by an enzymatic-spectrophotometric method (Gutmann and Wahlefeld, 1974). This method is based on the enzymatic conversion of L-lactate to pyruvate with the concomitant reduction of NAD to NADH. The increase in absorbance at 340 nm is proportional to NADH formation. The data is presented as the percentage of lactic acid production of each treated group relative to the corresponding non-treated control groups.

Viable Cell Counts

Each individual peg with a biofilm on it was cut off from the lid with a sterile scalpel without disturbing the biofilms and placed in 1 mL CPW (5 g yeast extract, 1 g peptone, 8.5 g NaCl, and 0.5 g L-cysteine hydrochloride per liter, adjusted to pH 7.3). Biofilms were dispersed by sonication on ice for 1 min with 1 s pulses at an amplitude of 40 W (Vibra cell TM , Sonics and Materials Inc., United States). Ten-fold serially diluted samples were plated onto BHI agar plates (100 µL/sample). The plates were incubated anaerobically for 3 days and colony-forming units (CFUs) were counted.

Statistical Analysis

The data were analyzed with the Statistical Package for Social Science (SPSS, Version 20.0). One-way analysis of variance (ANOVA) was used to compare the biofilm formation of the three S. mutans strains at 32 and 48 h, followed by a Bonferroni's post hoc test. An independent Student's t-test was further applied to compare the 32-and 48-h biomass formations of each strain. The difference was considered significant if p < 0.05. The percentage of biomass increase and lactic acid production relative to the control group of these three S. mutans biofilms to NaF, CHX, and low-pH treatment were analyzed by a two-way ANOVA analysis, using strains and treatment conditions as the independent variables. When the interaction between strains and treatment conditions was significant, new two-way ANOVA analyses were carried out for each of the three pairs of strains. The difference was considered significant if p < 0.016 after Bonferroni correction. All tests were performed for the biofilms formed in the constantly neutral pH and the biofilms formed in the pH-cycling separately.

RESULTS

In this study, three aspects of fitness were examined for all tested strains in the absence of NaF: biofilm formation, response to CHX treatment, and response to a low-pH challenge. In addition, the inhibitory effect of NaF on biofilm formation and lactic acid production was examined for these three strains to confirm the fluoride resistance of UF35 and UAFR in biofilms.

Biofilm Formation

The capability of biofilm formation of three strains, measured with the crystal violet staining assay, is presented in Figure 2. The biomass of these strains was measured after 32 and 48 h of incubation. Irrespective of the pH regime during biofilm formation and age, UAFR produced significantly more biomass than UF35 and UA159, whereas the latter two strains did not differ in biofilm formation. The viable-cell plate counts of the 48-h biofilms supported the results from the crystal violet staining assay. The log CFU per biofilms were: 8.1 ± 0.5 (neutral pH), 7.8 ± 0.3 (pH-cycling) for UAFR; 7.1 ± 0.4 (neutral pH), 7.3 ± 0.1 (pH-cycling) for UF35; and 7.4 ± 0.3 (neutral pH), 7.2 ± 0.3 (pH-cycling) for UA159. In accordance with the differences in biomass and CFU counts, the lactic acid production of the 48-h UAFR biofilms was also significantly higher than the other two biofilms. No difference in lactic acid production was observed between UF35 and UA159 biofilms regardless of the growth conditions (data not shown).

FIGURE 2 | Biomass of 32-and 48-h biofilms. The biofilms of Streptococcus mutans UA159, UF35 and UAFR were formed under either a constantly neutral pH or a pH-cycling condition for 32 and 48 h. The biomass was quantified by the crystal violet staining assay and presented as the OD value at 608 nm. * Indicates the significant difference between the 32-and 48-h biofilms of each strain, p < 0.05. Frontiers in Microbiology | www.frontiersin.org

Response of Biofilms to CHX and Low-pH Challenge

As stated above, S. mutans UAFR biofilms produced significantly more lactic acid than UF35 and UA159 biofilms. Therefore, the treatment efficacies of CHX and low pH are presented as the percentage reduction in lactic acid production of the treated samples relative to the non-treated samples (Figures 3, 4). Figure 3 shows that the reduction in lactic acid production in biofilms was enhanced with increasing concentrations of CHX. Under constantly neutral pH, the CHX concentrationdependent reduction in UAFR biofilms seemed to be the strongest among the three strains, but the differences did not reach statistical significance ( Figure 3A). However, under pH-cycling, this reduction in UAFR biofilms was significantly less than the reduction in the other two biofilms (Figure 3B). UF35 biofilms showed similar responses to the CHX treatment as the wild-type UA159 biofilms.

With increasing durations of the low-pH challenge, the reduction in lactic acid production in biofilms became more obvious (Figure 4). Again, S. mutans UAFR biofilms behaved differently from UF35 and UA159 biofilms, but the difference  The biofilms were formed under pH-cycling condition. The data are presented as the percentage of lactic acid production in low-pH treated groups relative to the corresponding non-treated control group. * Indicates the significant difference between treatment response of each strain, p < 0.016. was only observed for the biofilms formed under constantly neutral pH condition ( Figure 4A). Under this condition, UAFR biofilms displayed a delayed response (longer than 1 min) to the low-pH challenge, whereas the other two biofilms already showed reductions in lactic acid production after being treated for only 1 min. Moreover, the effect of the duration of the low-pH challenge varied upon the conditions of biofilm formation. When the biofilms were formed in the constantly neutral pH condition, the low-pH challenge reduced the lactic acid production of all biofilms to undetectable levels within 5 min, whereas this took 30 min when the biofilms were formed in pH-cycling condition.

Response of Biofilms to NaF Treatment

To confirm that the UF35 and UAFR biofilms are indeed less sensitive to fluoride than the wild-type UA159 biofilms, we examined the responses of these three biofilms to a growth medium containing NaF (Figure 5). The NaF treatment did not affect the biofilm formation of UAFR, but reduced that of UF35  biomass (A,B) and lactic acid production (C,D) of the biofilms are shown. The data are presented as the percentage of biofilm formation or lactic acid production in the NaF treated groups relative to the corresponding non-treated control group. * Indicates the significant difference between treatment response of each strain, p < 0.016. and, to a larger extent, that of UA159, in a dose-dependent manner (Figures 5A,B). In terms of lactic acid production, Figure 5C shows that under the neutral pH condition, UAFR biofilms were affected the least, followed by UF35 and then by UA159. The lactic acid production of UA159 biofilms dropped to around 28% of the non-treated group at 6 mM NaF, whereas that of the UF35 biofilms dropped to a level similar to the UA159 biofilms at 12 mM NaF. The lactic acid production of UAFR biofilms did not drop below 70%, even at 12 mM NaF. Figure 5D also shows a NaF concentrationdependent reduction in lactic acid production among three biofilms with one exception. At the pH-cycling condition, the reduction of lactic acid production in UAFR biofilms was only observed at 0.25 mM NaF, and no additional reduction could be observed with increasing NaF concentrations. The level of NaF resistance of three strains is generally ranked as follows:
UAFR > UF35 > UA159.
Because the treatment efficacy for NaF is known to be pH-dependent, the tested concentration range of NaF differed in the biofilms formed under two pH conditions, 3-12 mM for constantly neutral pH and 0.25-1 mM for the pH-cycling.

DISCUSSION

In this study, we investigated the fitness of two S. mutans fluorideresistant strains using their fluoride-sensitive wild-type parent strain as a reference. We measured the response of S. mutans strains to several concentrations of various antimicrobials. Instead of comparing the responses of S. mutans strains at each concentration, we examined the concentration-dependent responses. Our data showed that independent of pH conditions during biofilm formation, neither of the fluoride-resistant strains has a reduced fitness as compared to the fluoride-sensitive strain.

To the contrary, one of the strains, UAFR, displayed stronger fitness in biofilm formation, resistance to CHX (pH-cycling only; Figure 3B), and resistance to low-pH challenge (neutral pH only; Figure 4A) than the wild-type strain and the other fluorideresistant strain, UF35, in absence of fluoride. Moreover, the UAFR strain coped better with the NaF treatment than UF35. As stated above, these two fluoride-resistant strains differ in the number of chromosomal mutations. Strain UF35 contains one mutation in the promoter region of the fluoride antiporter-coding genes and resists fluoride challenge through up-regulation of fluoride antiporters (Liao et al., 2016). Strain UAFR was obtained by stepwise selection on agar plates containing increasing concentrations of fluoride (Zhu et al., 2012). The genetic mechanism of fluoride resistance in UAFR is still unknown. We have identified up to 21 single nucleotide polymorphisms (SNPs) in the UAFR genome by comparing its genome sequence with that of the wild-type strain UA159. One of these SNPs is located in the same promoter region of the fluoride antiporter genes as in the UF35 strain (data not shown). The differences in fitness and in fluoride resistance between UF35 and UAFR may be related to the number of chromosomal mutations in their genomes. In a previous study, a series of isogenic Escherichia coli strains carrying up to five fluoroquinolone resistance mutations were constructed and examined for the fitness cost resulting from fluoroquinolone resistance (Marcusson et al., 2009). The strains containing more than three mutations possessed a better fitness in growth rate in the absence of fluoroquinolone than those containing less than three mutations. In our study, the additional mutations in UAFR may lead to the observed improvement in fitness, including enhanced biofilm formation and resistance to CHX.

The fitness of a bacterium can be influenced by its growth conditions (Bjorkman et al., 2000). In this study, we observed that strain UF35, when grown in biofilms, responded similarly to the low-pH challenge as the wild-type strain, whereas it was previously found to be more susceptible to the same treatment than the wild-type strain when grown in suspension (Liao et al., 2016). Thus, the bacterial lifestyle can lead to differences in fitness. Similarly, we observed that the resistance of UAFR biofilms to CHX and a low-pH challenge also depended on the conditions of biofilm formation. The higher resistance of UAFR biofilms to a 1-min low-pH challenge could be due to the higher biomass of UAFR as compared to the wild-type strain. The treatment time (1 min) may have been too short to allow effective penetration of the acid solution into the dense biofilm layer. However, the resistance of UAFR to CHX treatment when the biofilms were formed in pH-cycling condition cannot be simply explained by its high biomass, because the same concentrations of CHX was applied to the biofilms formed in either pH condition. Further studies are necessary to investigate the role of the different gene mutations in the UAFR strain's resistance to CHX treatment.

As shown in the treatment design of this study (Figure 1), the duration of the low-pH challenge was much longer for the biofilms formed under pH-cycling conditions up to 30 min than for the biofilms formed under constantly neutral pH conditions up to 5 min. This increased resistance to the low-pH challenge might be related to the acid tolerance level of the biofilm formed in pH cycling conditions. It is known that S. mutans is able to alter its physiology under acidic conditions in order to survive: this adaptive response is referred as the acid tolerance response (ATR) (Welin-Neilands and Svensater, 2007). Several studies have demonstrated that planktonic cells and cells in biofilms survived acid killing better after a prior exposure to low but nonlethal pH values (McNeill and Hamilton, 2003;Welin-Neilands and Svensater, 2007). In our experiments, the biofilms formed in pH-cycling conditions have been exposed to pH 5.5 for 16 h before the acid killing treatment, which might trigger the ATR and result in stronger resistance to acid killing.

This study showed that a duration of 16 h was required to observe an inhibitory effect of NaF on the biofilms. It also determined the inhibitory concentrations of NaF on biofilms, being 3-12 mM when the pH of NaF solutions was neutral and 0.25-1 mM when the pH of NaF solutions was 5.5. Although these are in vitro findings, they are helpful in estimating the selective pressure that a daily usage of NaF can impose on the oral microbes. In vivo, the concentration of fluoride remaining in dental biofilms after application of fluoride-containing products was reported to be between 0.06 and 0.3 mM F (Duckworth et al., 1987;Naumova et al., 2012). In a healthy oral ecosystem, where the pH of dental biofilms is mostly neutral, the daily application of fluoride would not impose any selective pressure, because our data showed the effective treatment concentrations of NaF should be above 3 mM (57 ppm F) when the pH of NaF solution was neutral. However, this might not be the case for the dental biofilms in caries-susceptible subjects or at approximal sites, where the pH of these biofilms often remains low for an extended period of time (Jensen and Schachtele, 1983). Our data showed that the fluoride-resistant biofilms (UF35) produced significantly more lactic acid (1.05 ± 0.07 mM) than the fluoride-sensitive UA159 biofilms (0.76 ± 0.01 mM) in pH cycling conditions after being treated with 0.25 mM NaF (4.75 ppm F). In the caries-susceptible biofilms in vivo, the daily application of fluoride would likely promote fluoride-resistant strains. Therefore, we could not exclude the possibility that the lack of clinical fluoride-resistant S. mutans isolates might be related to low selective pressure despite the daily fluoride usage. Fluoride-resistant strains might only be present in a specific niche in the oral cavity.

In summary, this study compared the fitness of two fluorideresistant strains with their wild-type fluoride-sensitive parent strain. In the absence of fluoride, neither fluoride-resistant strain showed compromised fitness as compared to the wild-type strain. In addition, the fluoride-resistant strain that contains multiple chromosomal mutations exhibited better fitness than the wildtype strain and the other fluoride-resistant strain that contained only a single chromosomal mutation. To understand better the fate of fluoride-resistant strains in an oral cavity, the fitness of these fluoride-resistant strains may be examined in a model that resembles the oral environment. For example, in a multispecies biofilm model, the fitness can be studied in the presence of host factors and other oral microorganisms. In addition, the competition between fluoride-resistant and fluoride-sensitive strains could be examined in such a model.

AUTHOR CONTRIBUTIONS

Conceived and designed the experiments: YC, XW, and DMD. Performed the experiments: YC, HL, and DMD. Analyzed the data: YC, YL, BB, and DMD. Drafted the manuscript: YC, YL, BB, and DMD. Critically revised the manuscript: XW, WC, and CVL. All the authors approved the final version of the manuscript and agreed to be accountable for all aspects of the work.

FIGURE 1 |
1The experimental design of the biofilm formation and treatment. CV, crystal violet assay; Lac, lactic acid quantification.

FIGURE 3 |
3Response of 48-h biofilms to CHX treatment. The 48-h biofilms of S. mutans UA159, UF35, and UAFR were treated by CHX for 5 min. (A) The biofilms were formed under constantly neutral pH condition. (B) The biofilms were formed under pH-cycling condition. The data are presented as the percentage of lactic acid production in the chlorhexidine (CHX) treated groups relative to the corresponding non-treated control group. * Indicates the significant difference between treatment response of each strain, p < 0.016.

FIGURE 4 |
4Response of 48-h biofilms to low-pH challenge. The 48-h biofilms of S. mutans UA159, UF35, and UAFR strains were treated with pH 3.0 buffer solutions for various periods of time. (A) The biofilms were formed under constantly neutral pH condition. (B)

FIGURE 5 |
5Response of various biofilms to 16-h NaF incubations. The 32-h biofilms of S. mutans UA159, UF35, and UAFR were formed with various concentrations of NaF for 16 h under either constantly neutral pH (A,C) or pH-cycling condition (B,D). The
August 2017 | Volume 8 | Article 1630
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ACKNOWLEDGMENTSThis work was supported by the National Natural Science Foundation of China (81670983), and Guangdong Science and Technology Department (2015A020212004, 2013B021800060). The authors thank Prof. Zhimin Zhang for providing the strain UAFR.
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Numerical simulation of vertical Bridgman solidification of CdZnTe

Hanen Jamai
LabEM (LR11ES34)
University of Sousse
ESSTH Sousse
Rue Lamine Abbassi4011Hammam SousseTunisia

Bernard Pateyron
CNRS-SPCTS/CEC
12 rue Atlantis87068LimogesFrance

Habib Sammouda
LabEM (LR11ES34)
University of Sousse
ESSTH Sousse
Rue Lamine Abbassi4011Hammam SousseTunisia

M El Ganaoui
Lab. Energétique de Longwy -LERMAB/FJV
Université de Lorraine
LongwyFrance

Numerical simulation of vertical Bridgman solidification of CdZnTe
10.1051/smdo/2014003Received 8 February 2014 / Accepted 17 April 2014CdZnTe solidificationAxisymetric Bridgman Vertical (BV)ALE formulation
The solidification of the singular CdZnTe in axisymetric Vertical Bridgman (VB) cavity is investigated in the current study. The numerical approach is developed by using COMSOL Multiphysics software, which is based on finite elements method (FEM) with Arbitrary Lagrangian-Euleurian (ALE) formulation allowing treating the moving interface. Numerical aspects of different parameters that affect the solidification interface and present an important factor during the crystal growth's process are presented and analyzed. Especial attention will be paid to investigate the thermophysical properties such as thermal diffusivity, heat capacity. Thermal conductivity and the effect of thermal condition specially the effect of cold temperature T c which affects significantly the concavity and the convexity of the interface for specific ranges in the solidification of CdZnTe phenomena, but it is of great importance the crystal growth experts are not it given importance. It has been shown that this properties, the effect of T c , and the variation of interface velocity affect the solid/liquid interface shape and the crystal growth process.

Introduction

The vertical Bridgman method for crystal growth from the melt was firstly developed in 1925. Nowadays, it is the most useful technique for the growth of crystals. This technique is explained in Figure 1. Its perfections to control temperature gradients and to provide provides pure crystals of large sizes by allowing testing the boundary conditions of mass and heat transfer. Hence, such technique is widely utilized in order to produce II-VI compound semiconductor crystals. Their industrial applications are mostly concentrated in detectors and solar cell production fields. Among these semiconductors, the Cadmium zinc telluride (CdZnTe) is considered as one of the most important and promising applied materials for room-temperature c and X-ray spectroscopy. Despite the fact that great efforts have been made to produce high quality of CdZnTe dominated by the Bridgman method, its production still suffers from small device size and low quality.

The solid-liquid interface shape is specially determined by heat transfer in melt crystal growth process. The search focus in heat transfer during Bridgman growth are presented in references [1][2][3][4][5], these others studied the factors affecting the shape of the liquid-solid interface, such as the such as the thermal conductivities of the crystal, melt, and ampoule, simple furnace characteristics and latent heat generation. In particular, Adornato and Brown [6] examined the effect of furnace profiles and ampoule materials on interface shape and satisfactorily compared their results to experiments of Wang et al. [7]. Jasinski and Witt [8,9] clarified notable insights on how interface shape may be controlled in Bridgman processes and considered the growth of CdTe as an example system.

In the aim of better understanding the solidification phenomenon and solving the physical problem during the crystal growth, researchers have chosen to test them by implementing a number of different numerical methods that can predict both the shape and position of the phase change front that are compatible with the governing conservation equations in each phase [10]. For instance, one of the most used methods is the front tracking approach which solves weak formulations of these equations by interface tracking by remeshing both states at every temporal step [11]. However, it is known that such method is not appropriate to study solidification process of alloys that undergo a frequent ''mushy region'' instead of sharp interface. Furthermore, another used method is the enthalpy method which is an approach that fixes the energy equation by using coordinates transformation. On another hand, the interface position is recovered a posteriori [11] and an extension of such a front fixing approach has been proposed in literature in order to introduce and predict the convection phenomenon within the two mushy region phases [12][13][14]. El Ganaoui et al. [15][16][17] improved this method by implementing a timedependent enthalpy-porosity formulation for directional solidification, in which the energy equation is introduced by using the enthalpy variable computing implicitly the thermal Stefan condition at the interface with an implicit procedure.

The current work uses COMSOL Multi-physics software, to simulate solidification in Bridgman Vertical (BV) configuration during CdZnTe, which is an II-VI compound crystal growth. To the best knowledge of the authors, it seems that thermophysical properties such as thermal diffusivity, heat capacity,      and thermal conductivity have not been well investigated. In fact, these thermophysical properties have important factors in the Stefan equation and therefore have an effect on the solidification, interface of CdZnTe. It is worth mentioning that both governing parameters the temperature of the solid domain is not well studied in literature and the growth rate phenomena still need better understanding and we propose to address such issue in the present work. From this point of view, the main idea of the current investigation is to control the shape interface, in solidification process. In particular, we will focus on the various parameters that affect the concavity and convexity of the interface that are also an important factor in crystal growth, namely, the thermal conductivity, temperature of the solid domain, and growth rate.

Materials and methods

Physical properties of the materials

The physical properties of CdZnTe are listed in Table 1 [18,19]. It should be noted that these properties depend on the given temperature, and they are in accordance with the thermal boundary conditions, for each domains.

Physics model

The Bridgman crystal system is schematically displayed in Figure 1a. The furnace uses a tapered heating element to establish a linear temperature profile Figure 1b. The ampoule is    axially positioned at the center of the growth furnace. During the process, the cylindrical ampoule containing the material in the solid and liquid phase is fixed at the constant rate V t = 0. Because of the symmetry of the system, the right half of Figure 1c is taken as the calculation domain only supposed. There is only heat conduction between the melt and crystal.

We can assume that this problem can be considered as a two dimensional axis-symmetry one, the temperature field, the Stefan equations are expressed in the cylindrical coordinates system.

The energy equations for the melt and the crystal given by:
r K l rT l ð ÞÀqCp l @T l @t ¼ 0; ð1Þ r K s rT s ð ÞÀqCp s @T s @t ¼ 0:ð2Þ
The shape of the solid-liquid interface is a compulsory controlling factor that allows producing a single crystal in vertical Bridgman enclosure. This interface shape is predicted by heat transfer and primarily by the direction of the heat flux near the interface. This interface is governed by the Stefan's equation expressed as:
K s rT s ð ÞÂn À K l rT l ð ÞÂn ¼ qÁHV int :ð3Þ
The aforementioned parameters in the above equations K s , K l , q, Cp l , and Cp s are the thermal conductivities, the density, specifics heats, in solid (denoted by s) and liquid (denoted by l), respectively. Here, DH expresses the latent heat and V int denoted the velocity at the interface.  The boundaries conditions corresponding to the temperature field are as follows: the left and right boundaries are kept adiabatic while the upper, the lower, and the interface position are maintained at T h = 1400 K, T c = 1200, and T m = 1364 K, respectively.
(a) V int =0 (b) Vi nter = stefan equation (c) V int =10 -6 (d) V int =10 -7 (e) V int =10 -8 (f) V int =10 -10

Numerical tools

For solving the mathematical model industrial software has been used, namely COMSOL which essentially integrated MATLAB which includes mathematics and computation; data acquisition; modeling, algorithm development; simulation, and prototyping; data analysis, exploration, and visualization. On another hand, the MATLAB language is particularly well suited to designing predictive mathematical models and developing specific algorithms [20,21]. Where, these algorithms contain operations for linear algebra, partial differential, matrix manipulation, or differential equation solving, data analysis and statistics.

First results concerned the validation of the computational approach versus the mathematical model. For that a test validation has been defined and conducted. It refers to available experimental results with considering shaped solid/liquid interface.

Test code validation

The validation herein concerns the physical problem of CdZnTe solidification in Vertical Bridgman (BV). In fact, the choice of this configuration is based on the experimental data [22][23][24] for CdZnTe crystal growth: R = 0.0375 m, L = 0.20 m, the temperature of the Bridgman furnace the upper of them being at a higher temperature than the melting point while the lower one is below the melting point. Thus, the system is cooled from below, and the solidification process begins from the bottom of the ampoule.

We noticed the same shape interface between our numerical computations ( Figure 2b) and experimental ones (Figure 2a) in which the authors [18] presented the half of longitudinal section of grown ingot of CdZnTe. In fact, they mentioned, that the interface shape at the end of growth is concave toward the crystal, with interface bending of 3 mm Figure 2a. The same results are shown numerically Figure 2b and a good agreement is observed with those obtained by Sen et al. [18]. In fact, the same results are revealed by the current simulation in which the shape interface is concaved and the progress rate is found to be around 3 mm in 9 h.

Results and discussion

Our results concerned the solidification process of CdZnTe in the Vertical Bridgman (VB) configuration. In fact, we will present the different parameters which affect the solidification of CdZnTe, with the aid of numerical simulations.

As aforementioned, one of the main ideas of our investigation is to present a general study of different parameters that affect the quality of the single CdZnTe crystal. Especially, we will give a great importance to study the thermo-physical properties of CdZnTe in each domain (solid or liquid) such as the thermal diffusivity a, the specific heat Cp (at constant pressure), and the thermal conductivity, that all depend on the temperature and which are measured for both solid and liquid CdZnTe. In addition, thermal diffusivity is an important factor in the current investigation. In fact, not only it offers a convenient and accurate method of determining the thermal conductivity (k), but also it is a crucial parameter in the conduction equation which governs heat transfer during crystal growth [18]. In addition, these parameters have a great impact on the Stefan equation that interferes in the solidification interface process.

In fact, as shown in Figures 3a and 3b illustrating the profile of thermal diffusivity in both solid and liquid domains, we note that this diffusivity increases for temperature in the solid domain while it decreases with temperature in the liquid state. Indeed, one can note that the diffusivity goes through a sharp minimum in the region of melting point; the value in the liquid is higher than that in the solid just before the onset of melting. The same results are showed by Sen et al. [18], who treated the influence of thermal diffusivity for CdTe and Cd0.96Zn0.04Te.

However, their results are significantly different from those reported by Marina et al. [22] who claimed that thermal diffusivity increased sharply above the liquid temperature for Hg 1 -x Cd x Te.

In the same context, we study the shape of the heat capacity shown in Figures 3c and 3d in both the solid and liquid domain. Besides, as shown in Figure 3a, the heat capacity is observed to be progressively augmented in the solid domain until reaching a maximum of temperature, precisely at the value T c = 1260 K. Consequently, by approaching the melting temperature, the profile of thermal capacity undergoes a decreasing trend until reaching a constant value in the liquid domain Figure 3b.

Similarly, we propose now to study the thermal conductivity and its influence on the interface shape and position as determined, in this case. In fact, we observed that the profile of thermal conductivity Figures 3e and 3f is similar to that relative to thermal diffusivity in both solid and liquid domain as revealed in Figures 3a and 3b. This makes good sense because thermal conductivity is proportional to thermal diffusivity which expression is defined by a = k/qCp. In fact, it was found that the profile of solid thermal conductivity K s is more enhanced compared to K l in liquid state. Figure 4a shows the temperature according to the solidification of CdZnTe along the both liquid-solid state plotted as function of axial coordinate, where z = À0.01 m denotes the bottom tip of solid domain, and z = 0.20 m corresponds to both liquid and liquid states. This thermal profile is based on two linear segments designed to yield a gradient in the melt and a steeper cooling rate in the crystal [25]. And, the visualization of interface evolution denoted by the Figure 4b, proved that is increased with increasing time. Figure 5 shows the interface temperature parameter as function of time. In fact, as note that after the initial transient, the temperature presented a peak which decreases steadily until a mild increase near the end of the run. The decreasing peak temperature coincides with decreasing melt height and volume as growth occurs. It is worth mentioning that similar results have been revealed by Cerny et al. [26], which mentioned that the time development of interface temperatures reveals well the establishment of the pseudo-steady regime of crystal growth after 15 h, and by Zang et al. [27] in the problem of solidification of CdZnTe crystal growth from the melt.

Thereafter, we will present the effect of the thermal conductivities ratio defined by K in the shape interface. We found that it is of great importance, because it changes not only the sign of curvature and consequently the concavity and the convexity of the interface shape, but also the curvature magnitude. Therefore, it was argued that for T h = 1400 K, T c = 1200 K and T m = 1364 K, the parameter K ensures the achievement of a convex interface when it is less than 1.1 and over which the interface becomes concave Figure 6. Therefore, it is to conclude that the conductivity ratio is of great importance in the CdZnTe solidification because it helps controlling the process of crystal growth.

Among the problems encountered in numerical simulation is the interface computation. These problems are generally called Stefan problems (Eq. (3)) that connects the axial temperature gradient in the liquid and the solid domain by the velocity growth. In fact, we devote this section to study the evolution of velocity interface for different values taken in the solidification of CdZnTe. The main issue in this section is to give a better visualization of the velocity growth and surface evolution which will allow to better understand the phenomenon of growth, especially the evolution and of the interface shape Figure 7 of great interest in this portion is to vary the velocity interface while keeping the speed of the bulb at zero, in other words the bulb is held fixed. The velocity profile depicted in Figure 7 demonstrates that the velocity value determined by the Stefan equation is strengthened compared to that computed during the growth of CdZnTe especially in the solidification of the material. This value is seen to be nearly 10 À5 m/s given by COMSOL after resolution and compilation of the Stefan equation while respecting the requirement for thermal boundary conditions s in both liquid and solid areas.

It was also noted that the decrease of the interface velocity from 10 À5 to 10 À10 m/s has a great effect on the evolution and the interface shape which becomes progressively weakened in Figure 8. Therefore one can conclude that the velocity variation is an important factor in the industrialization of crystal growth.

In this part we attempt to focus on predicting the effect of the variation of cold temperature T c on the isotherms in the liquid state which they are affected by the advancement of the shape interface and consequently the concavity and the convexity magnitude. In fact, as we mentioned before in the introduction, although this factor is also important in the understanding of crystal growth industrialization, it has not been well investigated until now. As revealed from Figure 9, we can mention that the variation of T c affects the concavity and the convexity of the interface. In fact, for T c 2 [1200 K À 1264 K], the interface remains concave while it becomes convex for T c 2 [1265 À 1354 K] especially, when the cold temperature reaches the value T c = 1265 k according to the fixed values T h = 1400 K, T m = 1364 K, and R = 0.037. However, by increasing T c over the value 1354 K, the problem is seen to diverge because the temperature approaches the specific value of T m .

We can finally conclude that the variation of T c is of great importance such as the thermal conductivities ratios and the velocity interface variation, and this parameter can help to solve some problems encountered during the growth of CdZnTe, especially the problem of the concavity and convexity of the interface shape which affects the quality of crystal growth.

Do not forget also that the purpose of any study is to solve the problems not only in the semiconductor factory, but also to obtain crystals of good qualities. Investigations must help to choose the value of the cold temperature which allow operators to obtain a concave or convex interface

In the same as mentioned in Figure 10 the variation of axial coordinate with radial coordinate for different values of cold temperature which reveals the same interpretation proved in Figure 9.

Our numerical findings may contribute in controlling the parameters for the growth process, and it represents a strong support to resolve difficulties for experimentalists.

Conclusion

In the current investigation, solidification of the singular CdZnTe in axisymetric Vertical Bridgman (VB) cavity is studied. All numerical computations are obtained using COMSOL Multiphysics software, which is based on finite elements method (FEM) with ALE (Arbitrary Lagrangian-Euleurian) formulation allowing treating the interface displacement. The visualization of temperature fields in terms of isotherms and spatial and temporal profiles and according to the solidification of CdZnTe is presented and discussed with the help of COMSOL to provide a better understanding of phase change. Especial attention has been attributed to study the thermo-physical properties of CdZnTe in each domain (solid or liquid) such as the thermal diffusivity a, the specific heat Cp (at constant pressure), and the thermal conductivity, which are measured for both solid and liquid CdZnTe. In this context, it is found that iso-surfaces of thermal diffusivity in both solid and liquid domains show that diffusivity increases for temperature in the solid domain while it is lowered with temperature in the liquid state. Furthermore, the diffusivity goes through a sharp minimum in the region of melting point and the value in the liquid is higher than that in the solid just before the onset of melting. In addition, the heat capacity is observed to progressively augment in the solid domain until reaching a maximum of temperature, at exactly the value T c = 1260 K. On another hand, it is found that the variation of T c affects the concavity and the convexity of the interface. In fact, it is seen that for specific interval of T c the interface remains concave while it becomes convex for another one. Concerning the effect of the interface velocity variation, it is found that the decrease of the interface velocity from 10 À5 to 10 À10 m/s has a great influence on the evolution and the interface shape which becomes progressively weakened. In this vein, analysis of the results shows that the velocity variation is seen to be an important factor in the industrialization of crystal growth.

Figure 1 .
1System. (a) Vertical Bridgman, (b) design domain, and (c) isotherms profile.

Figure 2 .
2Comparison between experimental data obtained by Sen et al.[18] (a) and our numerical results (b) in terms of the interface growth of CdZnTe.

Figure 3 .
3Thermal diffusivity, Specific heat and Thermal conductivity of CdZnTe relatively to the solid domain (a) and the liquid one (b), respectively for fixed parameters T c = 1200 K, T m = 1364 K, and T h = 1400 K.

Figure 4 .
4Vizualisation of temperature field, and the spatial and temporal variations of the interface evolution in both solid and liquid domains.

Figure 6 .
6Influence of thermal conductivity ratio K = K l /K s on the interface shape for T c = 1200 K, T h = 1400 K, and T m = 1364 K.

Figure 5 .
5Temporal variation relative to the temperature at the interface for T h = 1400 K, T c = 1200 K, and T m = 1364 K.

Figure 7 .
7Temporal and spatial variations of isovalues relative to the interface velocity.

Figure 8 .
8Effect of the interface velocity on the interface shape for T c = 1200 K, T h = 1400 K, and T

Figure 9 .
9Isotherm patterns with respect to different values of the cold temperature T c for T h = 1400 K and T m = 1364 K.

Figure 10 .
10Effect of the cold temperature on the interface shape at fixed parameter values T c = 1200 K, T h = 1400 K, and T m = 1364 K.

Table 1 .
1Physical properties of CdZnTe.Property
Temperature
Polynomial
Conductivity, W/(K m)
500 K < T < 1200 K
5.337 À 2.263 · 10 À3 T
1200 K < T < 1364 K
À 38.31 + 6.78 · 10 À2 T À 2.811 · 10 À5 T2
T > 1364 K
9.987 À 5.676 · 10 À3 T
Specific heat Cp, J/(Kg K)
298 K < T < 1600 K
177.8 + 1.663 · 10 À1 T À6.607 · 10 À5 T2 + 1.703 · 10 À8 T3
Heat of fusion DH, J/Kg
209 000
209 000
Expansion coefficient
T > 525 K
6.3629 · 10 À6
Melting point T m , K
1364
-
Density Kg/m 3
-
5680

(a)
(b)
(c)

Solid
state

Solid/liquid
Interface

Liquid
state

H. Jamai et al.: Int. J. Simul. Multisci. Des. Optim. 2014, 5, A23
Acknowledgements. The fist author thanks Profs. R. Bennacer (ENS Cachan) and A. Aydi (university of sfax) for fruitful discussion.
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Numerical simulation of vertical Bridgman solidification of CdZnTe. H Jamai, B Pateyron, H & El Sammouda, M Ganaoui, Int. J. Simul. Multisci. Des. Optim. 523Cite this article asCite this article as: Jamai H, Pateyron B, Sammouda H & El Ganaoui M: Numerical simulation of vertical Bridgman solidification of CdZnTe. Int. J. Simul. Multisci. Des. Optim., 2014, 5, A23.