Open Access Nano Express

Structural evolution of GeMn/Ge superlattices grown by molecular beam epitaxy under different growth conditions

Ya Wang1, Zhiming Liao1, Hongyi Xu1, Faxian Xiu2, Xufeng Kou4, Yong Wang13*, Kang L Wang4, John Drennan5 and Jin Zou15*

Author Affiliations

1 Division of Materials, The University of Queensland, Brisbane, QLD 4072, Australia

2 Department of Electrical and Computer Engineering, Iowa State University, Ames, IA, 50011, USA

3 Department of Materials Science and Engineering, Zhejiang University, Hangzhou, 310027, China

4 Department of Electrical Engineering, University of California at Los Angeles, CA, 90095, USA

5 Centre for Microscopy and Microanalysis, The University of Queensland, Brisbane, QLD 4072, Australia

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Nanoscale Research Letters 2011, 6:624  doi:10.1186/1556-276X-6-624

The electronic version of this article is the complete one and can be found online at:

Received:19 September 2011
Accepted:12 December 2011
Published:12 December 2011

© 2011 Wang et al; licensee Springer.

This is an Open Access article distributed under the terms of the Creative Commons Attribution License (, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


GeMn/Ge epitaxial 'superlattices' grown by molecular beam epitaxy with different growth conditions have been systematically investigated by transmission electron microscopy. It is revealed that periodic arrays of GeMn nanodots can be formed on Ge and GaAs substrates at low temperature (approximately 70°C) due to the matched lattice constants of Ge (5.656 Å) and GaAs (5.653 Å), while a periodic Ge/GeMn superlattice grown on Si showed disordered GeMn nanodots with a large amount of stacking faults, which can be explained by the fact that Ge and Si have a large lattice mismatch. Moreover, by varying growth conditions, the GeMn/Ge superlattices can be manipulated from having disordered GeMn nanodots to ordered coherent nanodots and then to ordered nanocolumns.

PACS: 75.50.Pp; 61.72.-y; 66.30.Pa; 68.37.L.

ferromagnetic semiconductor; transmission electron microscopy; magnetic precipitation; molecular beam epitaxy


Since their discovery in the early 2000s [1,2], Mn-doped Ge-diluted magnetic semiconductors [DMS] have been extensively investigated due to their good compatibility with mainstream Si technology [3-14]. In order to obtain room temperature ferromagnetism, enormous efforts were devoted to the growth of high-quality defect-free GeMn DMS. However, in most cases, Mn-rich precipitates (e.g., Ge3Mn5 [4,6] and Ge2Mn5 [15]) tend to form during growth due to the low Mn solubility in Ge. It has also been found that the thickness of GeMn thin films plays a critical role in the formation of Mn-rich precipitates, and secondary precipitates are usually easier to nucleate in thicker thin films due to the active Mn diffusion [15]. Therefore, it is desirable to grow thinner films to avoid Mn-rich precipitates. Using this strategy, we previously fabricated precipitate-free Ge0.95Mn0.05 quantum dots with Curie temperature up to 400 K [7] and demonstrated electrical-controlled ferromagnetism. On the other hand, for practical applications, it is desirable to control the distribution of Mn and to avoid the formation of Mn-rich secondary phases. By employing a 'superlattice' method, we successfully obtained ordered GeMn nanodot arrays [16]. These nanodot arrays exhibit unique magnetic properties and show promising applications in spintronic devices. However, the effects of substrate, Mn concentration, and growth temperature on the behavior of the GeMn nanodots are not yet explored although it is critical to fundamentally understand the structural evolution of such ordered nanodots.

In this study, by transmission electron microscopy [TEM], we investigated the effect of substrate, GeMn/Ge thickness, Mn concentration, and growth temperature on the structure of GeMn nanodots grown by molecular beam epitaxy [MBE]. We observed a structural change from being disordered GeMn nanodots to ordered nanodots and then to ordered nanocolumns by varying the growth conditions. The reason behind this phenomenon is also discussed.

Experimental details

Following a well-established growth approach [8,16], ten periods of GeMn/Ge superlattice were grown on various substrates (Si, Ge, and GaAs) at different temperatures (from room temperature to 150°C) by a PerkinElmer MBE (SVT Associates, formerly Perkin-Elmer, Physical Electronics Division, Eden Prairie, MN, USA), and the growth details are summarized in Table 1. By adjusting the Mn cell temperature, the Mn concentration of the GeMn layer can be changed. For example, when the Mn's cell temperature was set as 900°C, the nominal Mn concentration in the grown GeMn layer is approximately 12%. In Table 1, the nominal Mn concentrations in different GeMn layers were adjusted by the Mn's cell temperature. During the growth, reflection high-energy electron diffraction technique was applied to monitor the surface of the grown thin films. The detailed growth information can be found in the study of Wang et al. [16]. The grown thin films were then characterized by various TEM techniques on a Philips Tecnai F20 TEM (Philips Co., Holland, The Netherlands) operating at 200 kV.

Table 1. Sample details

Results and discussions

The effect of substrates

Figure 1a, b, c shows typical cross-sectional bright-field TEM images taken from samples S1 to S3 and shows GeMn/Ge superlattices grown on Ge, GaAs, and Si substrates under the same growth conditions, respectively. Ordered GeMn nanodot arrays are observed in Figure 1a, b, indicating that GeMn nanodot arrays can be formed both on Ge and GaAs substrates. However, no ordered nanodots were seen in the superlattice grown on Si substrates, as illustrated in Figure 1c. To understand the structural characteristics of grown nanodots, high-resolution TEM investigations were performed, and examples are shown in Figure 1d, e. As can be seen in Figure 1d, ordered and coherent GeMn nanodots can be clearly observed when they are grown on Ge or GaAs substrates. However, precipitates (moire fringe marked in Figure 1e) and lots of stacking faults appeared in the thin films grown on Si. Interestingly, a large number of voids can also be seen at the interface of the GeMn thin film and Si substrates. Since the lattice constant of Ge which is 0.5656 nm [17], close to that of GaAs (0.5653 nm), is larger than that of Si (with a lattice constant of 0.543 nm) [17], there should be almost no lattice mismatch occurring in the Ge/GaAs interface, but only a 4.35% lattice mismatch between the Si and Ge substrates. For this reason, the GeMn/Ge superlattices can be well epitaxially grown on both Ge and GaAs substrates, but for Si substrates, to release the strain induced by the lattice mismatch, the formation of stacking faults, voids, or precipitates will be hardly avoided [18]. It is also interesting to note that the nanodots grown on GaAs substrates seem better than those on Ge substrates. As those films were grown at the same condition, and GaAs has a nearly identical lattice constant as Ge, this phenomenon may be caused by other factors, such as different thermal coefficients for Ge and GaAs [19].

thumbnailFigure 1. Typical, high-resolution, and high-magnification TEM images of superlattices, nanodots, and interface. Typical TEM images of GeMn/Ge superlattices grown on (a) Ge, (b) GaAs, and (c) Si." . (d) A high-resolution TEM image of GeMn nanodots in (a). (e) A high-magnification TEM image of GeMn/Si interface.

The effect of Ge/GeMn thickness

It should be noted that coherent and ordered MnGe nanodot arrays require a critical growth window to ensure its reproducibility [16]. It is expected that a larger Ge spacer layer or a narrower MnGe layer would give rise to less strain coupling from the two adjacent MnGe layers, resulting in less ordered MnGe nanodots. In contrast, a thinner Ge spacer layer or a thicker MnGe layer (with more strain coupling) would cause vertically coalesced nanodots. Indeed, by decreasing the MnGe layer thickness to 1.2 nm while keeping other growth parameters identical, disordered MnGe nanostructures were observed (Figure 2a). On the other hand, when the Ge spacer layer was reduced to 4.6 nm, well-aligned Mn-rich nanocolumns with an Mn concentration up to 19% could be achieved (Figure 2b, e). Nevertheless, for both cases, coherent GeMn nanodots/nanocolumns can be observed, as displayed in the high-resolution TEM images in Figure 2c, d (for samples S4 and S5, respectively).

thumbnailFigure 2. Typical, high-resolution, and scanning TEM images of samples. Typical TEM images of samples with different spacer thickness (a) S4 and (b) S5. High-resolution TEM images of samples (c) S4 and (d) S5. (e) A scanning TEM dark field image of sample S5.

The effect of Mn concentration

Other than the variation of the MnGe and Ge layer thicknesses, the change of Mn concentration can also be employed to control the behaviors of grown MnGe nanostructures. As shown in Figure 3, by varying the Mn concentration, the following sequence can be observed: disordered GeMn nanodots, ordered nanodots, and then ordered nanocolumns. Indeed, less Mn doped in Ge may not induce enough strain, which is critical to provide a nucleation site for the subsequent GeMn deposition. As a consequence, disordered GeMn nanodots are formed, as displayed in Figure 3a, b, c. On the other hand, by increasing the Mn concentration, the increased strain makes the two nearest vertical nanodots more easily merged and subsequently, the formation of nanocolumns (refer to Figure 3e). With an optimal Mn concentration between the two cases, the ordered GeMn nanodots can be formed without changing other growth parameters, as shown in Figure 3d.

thumbnailFigure 3. Typical TEM images of samples with different Mn concentration. Samples (a) S6, (b) S7, (c) S8, (d) S1, and (e) S9.

The effect of growth temperature

Finally, the effect of the growth temperature on the MnGe nanostructures is investigated, and the results are shown in Figure 4. By comparing the morphology of Figure 4, the optimal temperature to secure the ordered and self-assembled nanodot arrays can be determined to be around 70°C. Since the Mn diffusion, promoting the formation of Mn-rich clusters, is closely related to the growth temperature, it is not active at lower growth temperatures, and less strain is induced, which would result in less ordered nanodots (refer to Figure 4a). However, higher growth temperatures cause the coalescence of the nearby nanodots and/or the possible formation of the secondary-phase Mn-rich clusters (for example Mn5Ge3 and Mn11Ge8) when the Mn diffusion is active, as shown in Figure 4c, d. For this reason, there should be an optimal growth temperature for the growth of ordered GeMn nanodot arrays.

thumbnailFigure 4. The effect of the substrate temperature. (a) S10 (27°C), (b) S1 (70°C), (c) S11 (110°C), and (d) S12 (150°C). The optimized growth temperature is found to be 70°C, as shown in (b).

According to our systematic study, the nanodot arrangement of the grown GeMn/Ge superlattices is sensitive to the growth conditions, such as substrate, Mn concentration, GeMn layer thickness, and growth temperature. There should be an optimal growth temperature and Mn concentration to secure the ordered nanodot arrays. Higher growth temperature and/or higher Mn concentration lead to the formation of Mn-rich secondary precipitates.


In conclusion, we have studied the effect of substrate, GeMn/Ge thickness, Mn concentration, and growth temperature on the structure of the GeMn/Ge superlattices grown by MBE. We found that by varying the growth parameters, the structure of the GeMn/Ge superlattices can be changed from disordered GeMn nanodots to ordered GeMn nanodot arrays and then to well-aligned GeMn nanocolumns.

Competing interests

The authors declare that they have no competing interests.

Authors' contributions

YW and FX conceived the study. YW and ZML carried out the experiments and analysis. HX, XF, JD, KW, and JZ participated in the design of the study and contribute to the analysis. YW, JZ, and YW wrote the manuscript. All authors read and approved the final manuscript.


The Australia Research Council, the Focus Center Research Program - Center on Functional Engineered Nano Architectonics (FENA), and the Western Institution of Nanoelectronics (WIN) in UCLA are acknowledged for their financial supports of this project.


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