# Effects of Phosphorus Diffusion on Gettering of Metal Impurities in UMG Silicon Wafers

Authors: Sung Yean Yoon; Jeong Kim; Kyoon Choi
Journal: International Journal of Photoenergy
 (2013)

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## Abstract

Fe distributions were simulated by using impurity-to-efficiency simulator for the analysis of phosphorus diffusion gettering and confirmed the dependencies of the electron lifetime on the various gettering conditions. It was observed that iron atoms in the Si wafer could be more efficiently gettered if the temperatures were provided to the wafer in two different steps. That two-step gettering process was applied to an upgraded-metallurgical grade (UMG) Si wafer, and the electron lifetimes of the UMG-Si wafer were 3μsec by applying the second temperature profile at 600°C for 420 min. It was also confirmed that the efficiency of the UMG-Si solar cell increased 0.53% due to two-step gettering process.


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## Body

## 1. Introduction

In order to reduce manufacturing costs, solar cells are usually produced with a multicrystalline silicon wafer, which inherently contains many impurity atoms and defects. In addition, many researchers have proposed that a further decrease in manufacturing costs could be obtained by using a UMG silicon wafer for the crystalline silicon solar cell [1]. However, more impurity atoms and defects remain in the cost-effective UMG silicon wafer than in the usual multicrystalline silicon wafer. UMG silicon wafers with 5 N purity include various kinds of transition-metal impurities. The high impurity concentration does not allow for the direct use of the UMG-Si wafers for solar cells. Thus, a variety of efforts have been devoted to increasing the purity of the UMG-Si wafers to the level of solar-grade silicon (SG-Si) wafers [2]. Transition-metal impurities, such as Fe, Ni, Cu, and Co, severely degrade the charge carrier lifetime by forming recombination centers in the band gap. Due to the generally high charge carrier recombination activity of transition metals and their precipitates, the presence of such contamination may limit the electrical performance of UMG-Si wafers and solar cells [3]. Generally UMG-Si is three orders of magnitude less pure compared with electrical-grade silicon (EG-Si), but the performance of high-quality UMG-Si solar cells has been demonstrated to be comparable to that of typical EG-Si counterparts [4].The gettering process has been a widely used method for reducing unintentional metal impurities in the electrically active zones of semiconductor devices. In addition to extrinsic gettering by means of phosphorus diffusion, various alternative methods such as scratching, sand-blasting, and ion implantation of various elements have been developed. Phosphorus diffusion gettering, which can efficiently reduce transition-metal impurities in the bulk of UMG-Si wafers and enhance the charge carrier lifetime, is a well-known process for improving the performance of solar cells in the PV industry [5].In spite of the enormous studies on the phosphorus gettering process, a clear explanation on the mechanism has not been announced so far. However, it was confirmed experimentally [6] and theoretically [7, 8] that the segregation of iron to phosphorus doped layer was the main factor to determine the efficacy of the phosphorus diffusion gettering. Hofstetter et al. developed the impurity-to-efficiency (I2E) simulation tool and calculated changes in the distribution of iron and phosphorus atoms during annealing [9]. In the simulation with I2E simulator, iron is considered as the dominant lifetime-limiting impurity, and this approximation is accurate in many regions of a standard mc-Si ingot. The I2E simulator was also used to predict the final solar cell performance with given inputs of material quality, cell processing conditions, and cell architecture.In this study, a phosphorus diffusion process was employed to getter the metal impurities in UMG-Si wafers. The distribution of iron atoms, the charge carrier lifetime of the UMG-Si wafer, and the efficiency of the cell were compared with the predicted values from the I2E simulator.A double side emitter was formed by using a POCl3 source to diffuse phosphorus at the front and back sides of UMG-Si wafers. An increase in the electron lifetime was confirmed by using the quasisteady state photoconductivity (QSSPC) measurement, and the efficiency of the UMG-Si solar cells was measured to determine the effectiveness of phosphorus diffusion gettering.


## 2. Experiments

P-type UMG-Si wafers with areas of 2.54 cm × 2.54 cm and thicknesses of 180–220μm were used. The particles and the organic compounds on their surfaces were removed with RCA-1 solution mixed with NH4OH, H2O2, and deionized (DI) water. The surface texturing was carried out using HNO3 and HF solutions, and the metal impurities on the surface were removed using RCA-2 solution mixed with HCl, H2O2, and DI water. The n+ emitter was formed by diffusing phosphorus into the wafer in a tube furnace. Phosphorus diffusion was performed by using liquid POCl3 as the dopant source carried by N2 gas. The temperature and time were varied in the ranges of 600–850°C and 0–550 min during phosphorus diffusion. The effects of time and temperature on the MCLTs of the silicon wafers were compared with the values after the standard diffusion which generally processed at 850°C for 10 min. Phosphorus silicate glass (PSG) formed after phosphorus diffusion was removed by dipping the wafer in a 0.1 M HF solution for 40 seconds, and the emitter sheet resistance was measured using the four-point probe method. An antireflection coating (ARC) of silicon nitride (SiNx:H) with a thickness of approximately 70 nm was then deposited by using a plasma-enhanced chemical vapor deposition (PECVD) in order to reduce the surface recombination velocity. The rear surface of the silicon wafer was also passivated by depositing the same SiNx:H film for the measurements of the QSSPC. The surface passivation by using iodine was also performed, but significant differences were not obtained compared with the passivation method by using the PECVD-SiNx:H film. An aluminum layer with a thickness of about 2 μm for the back contact of the cell was deposited by RF-sputtering, and a silver electrode was formed on the front side by screen-printing. The RF-sputtered aluminum layer and the screen-printed silver were fired using a belt furnace at 800°C to form the front and back contacts.The average characteristics of the electron lifetime were obtained by using the QSSPC measurement system: a Sinton WCT-120 tester according to the carrier density at an injection level of 2 × 1014 cm−3. After gettering process, impurities in the bulk of the wafer move to the surface region. And, before measuring the electron lifetime, the surface of the UMG-Si was removed by chemical etching.


## 3. Simulation Process

The typical Fe concentration in the UMG silicon wafer was reported to be 27 ± 8 ppmw by Degoulange et al. [10]. Some of these iron atoms exist at the interstitial sites or Fe-B pairs, and the rest of the iron atoms remained as precipitates in the wafer. During the solar cell fabrication process at high temperature, iron atoms in the bulk of the silicon wafer segregate to a diffused phosphorus layer and are dissolved from iron silicide precipitates. Figure 1 shows the I2E simulation results for the distribution of phosphorus and Fe concentrations after the gettering process at 700°C for 300 min. The phosphorus concentration on the surface of the wafer was set to 3 × 1020 atoms/cm3 and the initial concentrations of Fe were 1 × 1015 and 1 × 1012 atoms/cm3 for the total and the interstitial Fe concentrations, respectively. That initial value of the total Fe concentration was assumed considering the total Fe concentration in the UMG-Si wafer. The segregation of iron atoms is described by Gafiteanu et al. [11] as
(1)∂Ci∂t=∂∂x[DFe(∂Ci∂x-Ciσ∂σ∂x)],
where Ci is the dissolved iron concentration, DFe is the temperature-dependent diffusion coefficient of iron in silicon, and x is the depth from the surface of the wafer. The first term on the right represents Fick’s law of diffusion, while the second term involves a space-dependent segregation coefficient, σ(x), which is characterized by the reactions between Fe interstitials, Si vacancies, and P dopant atoms [12]. Also, the dissolution of precipitated iron atoms is modeled by Ham’s law [13]:
(2)∂Ci∂t=4πNrDFe(Ceq,Fe-Ci),
where N is the precipitate density, r is the precipitate radius, and Ceq,Fe is the temperature-dependent solid solubility of iron in silicon. The dissolved iron atoms from the precipitated sites diffused to the P-abundant region, and the distribution of the Fe concentration in the Si evolved as shown in Figure 1. Secondary ion mass spectroscopy (SIMS) analysis was used to confirm the real distribution of iron atoms in the UMG-Si wafer annealed at 700°C for 5 hours after the P-diffusion process, as shown in Figure 1(e). The difference to the simulation results was mainly from the higher concentration of iron atoms in the UMG-Si and the slightly different gettering temperature and time.Calculated distributions of P dopant concentration, total Fe concentration, interstitial Fe concentration, and electron lifetime (from the upper graph) after the gettering process at 700°C for 30 min. The lowest graph is the bulk Fe concentration by means of SIMS measurement of the UMG-Si gettered at 700°C for 5 hours.
(a)
(b)
(c)
(d)
(e)After calculating the Fe distribution in the silicon, the I2E simulator determines electron and hole lifetime throughout the wafer thickness. Shockley-Read-Hall recombination is represented by the charge carrier lifetime [14] as
(3)1τi=Ciσcvth,
where τi is the minority carrier lifetime limited by interstitial iron or Fe-B pairs, σc is the minority carrier capture cross section, and vth is the thermal velocity of minority carriers. Recombination at iron silicide precipitates also contributes to the charge carrier lifetime by the following expression [15]:
(4)1τp=4πr2NsD/rs+D/r,
where τp is the minority carrier lifetime limited by precipitates, D is the minority carrier diffusion length in silicon, and s is the carrier recombination velocity at the precipitate surface. Figure 1(d) shows the electron lifetime obtained using the I2E simulator under the distributions of the P and Fe concentrations. In the figure, the electron lifetime was confirmed to be determined largely from the Fe concentration in the silicon. However, it is not clear which is the main factor between the total and the interstitial Fe concentrations in Figure 1.


## 4. Results and Discussion

Figure2 shows the simulation results of the total Fe concentration averaged throughout the Si wafer after the gettering process. The initial concentrations of the total and the interstitial iron atoms were assumed to be 1 × 1015 and 1 × 1012 atoms/cm3, respectively, and uniformly distributed in the wafer. The total Fe concentration reduced almost linearly with the gettering time, and the reduction rate rapidly increased with the temperature, which was due to the diffusion of iron atoms to the P-abundant surface layer in the Si wafer.Figure 2
Calculated total Fe concentration averaged throughout the Si wafer after the gettering process with different temperatures and times. The initial concentration of the total iron atoms was assumed to be 1 × 1015 atoms/cm3. The total Fe concentration decreased more rapidly with gettering time for higher temperature.On the other hand, the dependence on the temperature of the interstitial Fe concentration was different from that of the total Fe concentration as shown in Figure3. At the gettering temperature of 750°C the interstitial Fe concentration slightly increased and then was saturated along with the time. However, at gettering temperatures above 750°C, the rapid increases within a few minutes were observed for the interstitial Fe concentrations. The interstitial Fe concentration in the Si wafers processed below 750°C decreased with elapsed time and was finally saturated as shown in Figure 3. In the case of the single-crystalline silicon, the amount of the iron atoms transferred to the interstitial sites is very small compared to those that moved to the diffused phosphorus layer from the interstitial sites, due to the initially low concentration of iron atoms in the bulk. Meanwhile, there are several orders of magnitude more iron atoms in the UMG-Si at interstitial or nondissolved precipitate sites in the bulk, compared with those in the single-crystalline silicon. This means that the amount of the iron atoms transferred to the interstitial sites competes with that moved to the diffused phosphorus layer from the interstitial sites and the interstitial Fe concentration may increase at the high gettering temperature in case of the Si wafer with a large amount of iron atoms.Figure 3
Calculated interstitial Fe concentration averaged throughout the Si wafer after the gettering process with different temperatures and times. The initial concentration of the interstitial iron atoms was assumed to be 1 × 1012 atoms/cm3. For higher temperatures than 750°C, the interstitial Fe concentration increased with time, which might be originated from the increase of iron atoms migrated from the precipitate sites at higher temperature.Equations (3) and (4) assert that the charge carrier lifetime in the Si wafer is determined from the distribution of the Fe concentrations, which exist at the interstitial sites or as precipitates. Figure 4 shows the averaged electron lifetime calculated from the distributions of the iron atoms. Comparing with the Fe concentrations in Figures 2 and 3, it is clear that the electron lifetime was strongly dependent on the interstitial Fe concentration but not on the total Fe concentration. Most of the iron atoms precipitated in the Si wafer did not directly affect the charge carrier lifetime. On the other hand, only a portion of the iron atoms at the interstitial sites mainly determined the charge carrier lifetime in the Si wafer. This means that the reduction of the interstitial Fe concentration is more important to enhance the charge carrier lifetime and the efficiency of the solar cell.Figure 4
Variation of the averaged electron lifetime calculated from the distributions of iron atoms using I2E simulator. It was strongly dependent on the distribution of the interstitial Fe concentration.In order to efficiently getter iron atoms and increase the charge carrier lifetime, a two-step gettering process was introduced in this study. The two-step gettering process involves an annealing process at a high temperature followed by a similar annealing process at a lower temperature. In this simulation, the first step of the temperature profile was fixed to 850°C and 30 min, and the temperature and the time were varied during the second step of the gettering process. Figure5 shows the interstitial Fe concentration and the electron lifetime with the temperature and the time during the second step of the gettering process. The duration time of the second step was 30 min for the analysis of the temperature dependency (Figure 5(a)), and the evolution of the interstitial Fe concentration and the electron lifetime with the gettering time of the second step was simulated at the temperature of 600°C (Figure 5(b)), where iron atoms were most efficiently gettered. The interstitial Fe concentration reached below 2 × 1010 atoms/cm3, and the electron lifetime was more than 8 μsec. Compared with the results of Figure 4, the two-step gettering process was evidently more advantageous for the UMG-Si wafer.Calculated interstitial Fe concentration and the electron lifetime with (a) the temperature and (b) the time during the second step of the gettering process. The electron lifetime showed the highest value at the temperature of 600°C, where the interstitial Fe concentration indicated the lowest value. On the other hand, with the increase of the time they were saturated above 50 min.
(a)
(b)Figure6 shows the electron lifetime of the UMG-Si wafer processed with the two-step gettering. The first step of the temperature profile was fixed to 850°C and 50 min. During the second step, the temperature varied between 600 and 750°C for 420 min (Figure 6(a)) and also the gettering time increased to 540 min at the temperature of 600°C. Aside from the measured values of the electron lifetime, the overall behavior was very similar to the simulated electron lifetime as shown in Figure 5. The electron lifetime of the bare UMG-Si wafer was about 1 μsec and slightly increased to 1.5 μsec after only the first temperature profile of the two-step gettering process. A further increase in the electron lifetime to 3 μsec could be obtained by applying the second temperature profile at 600°C for 420 min. The difference in the values between the simulated and observed electron lifetime was originated from the higher total concentration of iron atoms in the UMG-Si wafer than in the sample assumed in this simulation. The grain boundaries in the UMG-Si wafer might be considered as the most important source of the impurities and act as precipitate sites. During the gettering process at high temperature, the precipitated iron atoms in the grain boundaries diffused into the interstitial sites and limited the further increase of the electron lifetime of the UMG-Si wafer.Electron lifetime of the UMG-Si wafer processed with two-step gettering. The first step of the temperature profile was fixed to 850°C and 50 min, and during the second step (a) the temperature and (b) the time were varied. The highest electron lifetime was obtained at 600°C for 420 min.
(a)
(b)Figure7 shows the I-V characteristics of the UMG-Si solar cells processed with one-step and two-step gettering. The efficiency of the cell with one-step gettering was 9.67%, and two-step gettering improved the efficiency of the cells to 10.2%. In this study, the fabrication process of the crystalline silicon solar cell was not optimized for the high-efficiency cell; instead the effect of phosphorus diffusion gettering on the efficiency of the cell was the main concern. The increase in the cell efficiency due to two-step gettering was 0.53%, which was largely due to increases in the short circuit current density, Jsc. On the other hand, open circuit voltage, Voc, of the cell processed with the two-step gettering did not increase compared with Voc of the cell processed with the one-step gettering in spite of the increase of the electron lifetime immediately after the gettering process. The two-step gettering was very effective to enhance the electron lifetime of the silicon wafer, which was due to the decrease of the interstitial Fe concentration not of the total Fe concentration. Thus, during the cell fabrication process at the high temperature after the gettering process, the interstitial Fe concentration which was closely related to the electron lifetime of the wafer might increase and Voc of the cell was not improved for the two-step gettering. This means that the low-temperature process is very important after the gettering process, especially for the UMG Si wafer which contains a large amount of impurities. Lin et al. reported that the gettering process may improve the diffusion length of a cell but had little influence on the efficiency of the cell [16], and the one-step gettering may also provide a gettering effect on the UMG-Si wafers. This points to the difficulties in obtaining a high-efficiency cell with low-quality material like the UMG-Si wafer.Figure 7
I-V characteristics of the UMG-Si solar cells processed with one- and two-step gettering. The increase in the cell efficiency due to two-step gettering was 0.53% compared with that from one-step gettering.


## 5. Conclusion

In this work, the Fe distribution and the electron lifetime of the Si wafer were calculated using I2E simulator for the analysis of phosphorus diffusion gettering. The total Fe concentration in the bulk of the Si wafer decreased with gettering time at the whole temperature range of 600–900°C suggested in this simulation scheme. Also, the total Fe concentration decreased more rapidly with gettering time for higher temperature. On the other hand, the interstitial Fe concentration, which largely determined the charge carrier lifetime in the Si wafer, increased with the gettering time at temperatures above 750°C and was saturated within a few minutes. In order to enhance the efficiency of the gettering, the two-step gettering process was introduced. The first step of the temperature profile at 850°C was followed by the second step at a lower temperature. At temperature of 600°C for the second step, the electron lifetime was optimized to 8μsec. This two-step gettering process was applied to the UMG-Si wafer, and it was observed that the electron lifetime of the UMG-Si wafer increased to 3 μsec after the two-step gettering process, compared with the electron lifetime of 1.5 μsec after the one-step gettering process. The improvement of the electron lifetime had a significant effect on the efficiency of the UMG-Si solar cell, and the increase in the cell efficiency due to two-step gettering process was 0.53% compared with that from one-step gettering process.



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