Abstract:
In a crystal growth method, a seed crystal  8  and a source material  4  are provided in spaced relation inside of a growth crucible  6 . Starting conditions for the growth of a crystal  14  in the growth crucible  6  are then established therein. The starting conditions include: a suitable gas inside the growth crucible  6 , a suitable pressure of the gas inside the growth crucible  6 , and a suitable temperature in the growth crucible  6  that causes the source material  4  to sublimate and be transported via a temperature gradient in the growth crucible  6  to the seed crystal  8  where the sublimated source material precipitates. During growth of the crystal  14  inside the growth crucible  6 , at least one of the following growth conditions are intermittently changed inside the growth crucible  6  a plurality of times: the gas in the growth crucible  6 , the pressure of the gas in the growth crucible  6 , and the temperature in the growth crucible  6.

Description:
BACKGROUND OF THE INVENTION 
     1. Field of the Invention 
     The present invention relates to sublimation growth of silicon carbide single crystals with low dislocation density. 
     2. Description of Related Art 
     Silicon carbide is an important wide-bandgap material used for the development and manufacturing of SiC and GaN semiconductor devices of new generation. While GaN-based devices are intended for the operation at microwave frequencies, SiC-based devices are aimed at efficient power switching. Other applications are also envisioned and are emerging. Silicon carbide is used as a lattice-matched substrate material to grow epitaxial layers of SiC and GaN. In order to produce low-defect epilayers and high-quality devices, the substrate must have good crystal quality, including low dislocation density. 
     Dislocations are one-dimensional crystal defects. They are generally categorized based on the value and direction of the so-called Burgers vector, which represents the magnitude and direction of the lattice distortion of dislocation in a crystal lattice, and a direction of a dislocation line. In silicon carbide, dislocations with their lines extending along the crystallographic c-direction are called threading. These include threading screw dislocations (TSD) and threading edge dislocations (TED), which have their Burgers vector not exceeding 1 or 2 lattice parameters. Micropipes are hollow-core threading screw dislocations with a larger Burgers vector, reaching in some cases hundreds of lattice parameters. Dislocations with their lines parallel to the basal c-plane are called basal plane dislocations (BPD). 
     For the measurements of the dislocation density in SiC, etching in molten KOH is generally employed to reveal dislocation-related etch pits. Often, the nature of the particular dislocation can be determined based on the characteristic shape of the etch pit. A photograph of an etched SiC surface (c-plane) is shown in  FIG. 1 . In general, etch pits due to TSDs are hexagonal and somewhat larger than those due to TEDs, which often appear more rounded. Etch pits due to BPDs are usually elongated and asymmetrical. 
     As an example, in a typical 7.62 cm diameter PVT grown 4H—SiC substrate, the TED and TSD densities are on the order of 5·10 4  cm −2  and 10 4  cm −2 , respectively, and the density of BPD can be 10 4  cm −2  or as high as 10 5  cm 2 . The total dislocation density can be as high as 3·10 5  cm −2 . The measured dislocation density depends both on the quality of the crystal and on the way wafers extracted from the crystal are sliced. Etching can reveal dislocations only if their lines intercept with the surface of the wafer. Therefore, wafers that are sliced parallel to the c-plane (on-axis) tend to exhibit lower densities of BPDs. 
     Moreover, the shape of etch pits in heavily nitrogen-doped n+SiC substrates are usually not well defined. A fraction of them have clearly elongated shapes and can be designated as BPD, all the rest have near circular shapes. 
     There are usually no distinctly hexagonal shaped dislocation etch pits. It is possible that this might be related to a low occurrence of screw dislocations in such crystals. More likely, it results from the effect of nitrogen dopant on the etching behavior of SiC, whereupon the distinction between TSD and TED diminishes. 
     Moreover, these etch pits tend to be slightly asymmetric. This may indicate a basal plane component in these dislocations as suggested in “Basal Plane Dislocation Dynamics in Highly p-Type Doped Versus Highly n-Type Doped SiC”, by P. J. Wellman et al., International Conference on Silicon Carbide and Related Materials, 2005, Pittsburgh, or it may simply reflect the impurity induced non-uniformity during etching. As a result, it is difficult to clearly separate different types of dislocations through molten KOH etching methods on these kinds of samples. However, this difficulty does not affect the measurement of total dislocation density. 
     For 4H—SiC homoepitaxy, an 4H—SiC substrate is generally oriented off its c-plane by 4 or 8 degrees in order to achieve regular step flow and eliminate nucleation of the 3C polytype. Consequently, most of the threading defects and a fraction of BPDs penetrate from the substrate into the epilayer. A large percentage of BPDs convert into TEDs at the interface between the substrate and the epitaxial layer. In addition, new defects can emerge at the substrate-epitaxial layer interface as a result of interaction between various types of dislocations and the step flow. These epitaxial layer defects are detrimental to device performance and include so-called comets and triangles, as reported in “Structure of Carrot Defects in 4H—SiC Epilayers”, by X. Zhang et al., International Conference on Silicon Carbide and Related Materials, 2005, Pittsburgh; and “Surface Morphology of Silicon Carbide Epitaxial Films”, by J. A. Powell et al., J. Electronic Mat., 24, (1995) p. 295. Although the exact nature of these defects is not yet completely understood, it is believed they are closely related to the dislocations in the substrate. 
       FIGS. 2A and 2B  are magnified photographs of epitaxial surfaces including a comet defect and a triangle defect, respectively. The photographs were taken on samples etched with molten KOH. Therefore, the surfaces also include a number of dislocation-related etch pits. As can be seen, both comet and triangle defects are bounded by dislocations. In particular, the comet is bounded by a TSD at one end and by a BPD at the other end. The triangle is bounded by two or more BPDs. 
     As is well-known to those skilled in the art of SiC growth and epitaxy, micropipes and dislocations have a detrimental impact on the efficiency and reliability of devices made with SiC, as reported in “Breakdown degradation associated with elementary screw dislocations in 4H—SiC p+n junction rectifiers” by P. D. Neudeck et al., Solid-State Electron. 42, (1998) p. 2157; and “Long term operation of 4.5 kV PiN and 2.5 kV JBS diodes”, by H. Lendenmann et al., Material Science Forum 353-356, (2001) p. 727. The reference “Bulk Crystal Growth, Epitaxy, and Defect Reduction of Silicon Carbide Materials for Microwave and Power Devices”, by J. J. Sumakeris et al., MRS Bulletin, Vol. 30, April (2005), p. 280 discusses device limitations due to the micropipes, TSDs, TEDs and BPDs that propagate from the substrate into the epi-layer. 
     In summary, reduction of dislocation density in the SiC substrate is crucial for minimizing the presence of harmful defects in epitaxial layers and for achieving improved characteristics of the devices. 
     The most common technique used for the growth of SiC single crystals by sublimation is Physical Vapor Transport (PVT). A schematic diagram of a PVT system  2  is shown in  FIG. 3 . Polycrystalline SiC grain, which serves as a sublimation source material  4 , is placed at the bottom of a graphite growth crucible  6  and a SiC seed crystal  8  is attached to a graphite lid or top  10  of crucible  6 . Loaded crucible  6  is heated to a growth temperature between 2000 and 2400° C. by way of a resistance heater (resistance heating) or an RF coil  12  (induction heating). A temperature difference is established between the sublimation source material  4  and seed crystal  8  in the presence of a low pressure (1-200 Torr) inert gas, such as helium or argon, inside crucible  6 , whereby the temperature of source material  4  is higher than that of seed crystal  8 . Under these conditions, source material  4  sublimes and fills the interior of the crucible  6  with a vapor comprised of silicon- and carbon-carrying volatile molecular species, such as SiC 2 , Si 2 C and Si. Driven by the temperature gradient, these species diffuse through the vapor phase in the direction from sublimation source material  4  to seed crystal  8 . Due to the lower temperature of seed crystal  8 , a supersaturation is created causing condensation of the vapor on seed crystal  8  and growth of a SiC single crystal  14  thereon. 
     The reference “Ultrahigh-quality silicon carbide single crystals,” by Nakamura et al., Nature 430 (2004), p. 1009, discloses growing SiC crystals with very low dislocation density, on the order of 100 cm −2 , using repeated a-face growth (RAF). This procedure included multiple sublimation growth runs. At each run, the growth direction was turned by 90 degrees. Although dramatically reduced dislocation density was observed, the RAF process is not conducive to volume manufacturing and, thus far, no recognizable body in the SiC crystal growth field has independently repeated or confirmed the results. 
     The total population of dislocations in SiC crystals can be divided into two groups: dislocations inherited from the seed and those generated during growth. Generation of dislocations during growth is believed to be due to the contamination of the growth interface by particles and other contaminants released from the source and graphite parts. Steep temperature gradients can lead to the excessive thermo-elastic stress and generation of dislocations. 
     Conventional and well-established measures can be applied to the PVT sublimation growth process in order to eliminate or reduce the generation of dislocations during growth. These measures include better purity of the growth components; degassing and vacuum baking of the graphite furniture and source at elevated temperatures; and moderation of the temperature gradients. 
     The reference “Basal Plane Dislocation Dynamics in Highly p-Type Doped Versus Highly n-Type Doped SiC”, by P. J. Wellmann et al., International Conference on Silicon Carbide and Related Materials, 2005, Pittsburgh, reports the study of the incorporation of an n-type layer during the growth of aluminum doped p-type SiC, using over-compensation by nitrogen, and followed the fraction of BPD in total dislocations through the crystal. The focus of the study was on the comparison between p-type and n-type doped SiC and the effect on BPD. The reference reported the increase in BPD fraction in the inserted n-type layer, and subsequent decrease of the fraction. The effect on the overall level of dislocation density was not reported. Furthermore, as previously discussed, the difference in the observed etch pit morphology between p-type and n-type SiC does not necessarily correspond to the nature of dislocations. It is possible that the etching behavior is modified by different impurities. There is no known technique that could be applied to minimize the propagation of threading dislocations from the seed into the growing crystal. 
     It would, therefore, be desirable to reduce the dislocation density in the SiC single crystals grown by sublimation and, more specifically, to minimize the propagation of the threading dislocations during growth from the seed into the growing crystal. 
     SUMMARY OF THE INVENTION 
     One embodiment of a crystal growth method comprises (a) providing a seed crystal and a source material in spaced relation inside of a growth crucible; (b) establishing in the growth crucible starting conditions for the growth of a crystal therein, said starting conditions comprising: (1) a suitable gas inside the growth crucible, (2) a suitable pressure of the gas inside the growth crucible, and (3) a suitable temperature in the growth crucible that causes the source material to sublimate and be transported via a temperature gradient in the growth crucible to the seed crystal where the sublimated source material precipitates; and (c) intermittently changing at least one of the following growth conditions inside the growth crucible a plurality of times during growth of the crystal: the gas in the growth crucible, the pressure of the gas in the growth crucible, and the temperature in the growth crucible. 
     In the method, each instance of intermittently changing at least one of the growth conditions can include changing said at least one growth condition from its starting growth condition and then returning said changed growth condition back to its starting growth condition after a period of time. The period of time can be the same or different for each instance of intermittently changing. 
     The suitable gas in step (b) can include at least one of the following: helium, argon and hydrogen. Changing the gas in step (c) can include adding nitrogen to the suitable gas of step (b). 
     The suitable gas pressure in step (b) can be a first pressure between 1 Torr and 200 Torr. Changing the pressure of the gas in step (c) can include increasing the gas pressure from the first pressure to a second pressure that is also between 1 Torr and 200 Torr. 
     The suitable temperature in step (b) can be a first temperature between 2000° C. and 2400° C. Changing the temperature in step (c) can include increasing or decreasing the temperature from the first temperature to a second temperature between 2000° C. and 2400° C. 
     The growth crucible can be disposed inside of a chamber into which the gas is introduced. The growth crucible can be comprised of a material, such as, without limitation, porous graphite, that is permeable to the gas. The chamber can be comprised of fused silica. 
     Another embodiment of a crystal growth method comprises (a) providing a growth crucible having polycrystalline source material and a seed crystal disposed in spaced relation therein; (b) heating the interior of the growth crucible such that a temperature gradient forms in the growth crucible between the source material and the seed crystal, the source material is heated to a sublimation temperature and the temperature gradient is sufficient to cause sublimated source material to be transported to the seed crystal where the sublimated source material precipitates on the seed crystal to form a growing crystal; (c) causing a gas to flow into the growth crucible that facilitates the transport of the sublimated source material to the seed crystal and the precipitation of the sublimated source material on the seed crystal; and (d) at plural times during the transport of the sublimated source material to the seed crystal and the precipitation of the sublimated source material on the seed crystal, alternately beginning and then terminating a change in at least one of the following: a mixture of the gas flowing into the growth crucible, a pressure of the gas flowing in growth crucible, and at least one the lowest and highest temperature of the temperature gradient in the growth crucible. 
     Beginning the change in the mixture of the gas flowing into the growth crucible can include adding to the gas of step (c) another gas that causes at least one of: an increase in the electrical conductivity of the growing crystal, a change in the visible color of the growing crystal, or a change in a lattice parameter of the growing crystal. Terminating the change in the mixture of the gas flowing into the growth crucible can include removing the other gas from the gas flow of step (c). 
     The other gas can be nitrogen. The gas of step (c) can include at least one of the following: helium, argon and hydrogen. 
     Beginning the change in the pressure of the gas flowing into the growth crucible can include increasing or decreasing the pressure of the flowing gas from a first gas pressure to a second gas pressure. Terminating the change in the pressure of the gas flowing into the growth crucible can include decreasing or increasing, respectively, the pressure of the flowing gas from the second gas pressure to the first gas pressure. Each gas pressure is desirably between 1 Torr and 200 Torr. 
     Beginning the change in the at least one of the lowest and highest temperature of the temperature gradient in the growth crucible can include increasing the temperature of the lowest temperature, the highest temperature, or both. Terminating the change in the at least one of the lowest and highest temperature of the temperature gradient in the growth crucible can include decreasing the temperature of the lowest temperature, the highest temperature, or both, back to the temperature(s) at the beginning of said change. 
     The temperature gradient can be between 10° C. and 50° C., or between 25° C. and 50° C. The lowest temperature of the temperature gradient can be 2000° C. The highest temperature of the temperature gradient can be 2400° C. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  is a magnified photograph of a potassium hydroxide etched SiC surface (c-plane) showing a threading screw dislocation (TSD), threading edge dislocations (TED) and a basal plane dislocation (BPD); 
         FIGS. 2A and 2B  are magnified photographs of potassium hydroxide etched epitaxial surfaces including a comet defect and a triangle defect, respectively; 
         FIG. 3  is a schematic diagram of a physical vapor transport (PVT) system for the growth of SiC single crystals by sublimation; 
         FIG. 4  is a schematic diagram of a PVT system for perturbation growth of SiC single crystals by sublimation in accordance with an embodiment of the present invention; 
         FIG. 5  is a flowchart of a method for perturbation growth of SiC single crystals in accordance with an embodiment of the present invention; 
         FIG. 6  is a cross section of a Boule grown in accordance with the disclosed method; and 
         FIGS. 7A and 7B  are enlarged photographs of a second-to-grow wafer and one of the last-to-grow wafers, respectively, obtained from the Boule of  FIG. 6 . 
     
    
    
     DETAILED DESCRIPTION OF THE INVENTION 
     The following detailed description will be made with reference to the accompanying figures where like reference numbers correspond to like elements. 
     It has been observed, that sharp perturbations of the SiC single crystal growth process can result in a noticeable reduction in the density of threading dislocations. One desirable way to induce such perturbation is by step-wise doping during growth. 
     Step-wise doping creates conditions where adjacent layers of the crystal grown in sequence have slightly different lattice parameters. As a result, a lateral stress component is created which forces each threading dislocation to change the direction of its line in order to avoid or eliminate this stress. Desirably, the direction of each dislocation line changes by 90 degrees, i.e., the dislocation from threading becomes basal. Accordingly, the probability for the dislocation to intersect an opposite sign dislocation located nearby increases. In addition, basal plane dislocations thus formed will no longer propagate in the direction of further crystal growth (c-direction). Step-wise doping carried out multiple times during SiC single crystal growth has been observed to significantly lower the dislocation density. 
       FIG. 4  is a schematic drawing of one non-limiting embodiment of a system for perturbation growth of SiC single crystals. In  FIG. 4 , PVT sublimation growth of silicon carbide is carried out in a graphite growth crucible  6  sealed with a graphite lid  10 . Desirably, crucible  6  and lid  10  are made of high-density, fine-grain and low-porosity graphite, such as “ATJ” available from Union Carbide Corporation of Danbury, Conn., under registered trademark UCAR® (registration number 1008278), or similar. Growth crucible  6  is loaded with a SiC polycrystalline source material  4  and a single crystal SiC seed crystal  8 . Source material  4  is disposed in a lower portion of crucible  6  while seed crystal  8  is disposed at the top of crucible  6 , desirably attached to lid  10 . Source material  4  can be contained in a thin-walled graphite source crucible  5 , which can be disposed spaced from the interior walls and base of crucible  6  (as shown) in any suitable and/or desirable manner. However, this is not to be construed as limiting the invention since it is also envisioned that source material  4  can be disposed in the bottom of crucible  6  as shown in  FIG. 3 . 
     Growth crucible  6 , loaded with source material  4  and seed crystal  8 , is placed inside a sealed chamber  16 , desirably made from fused silica. A means for heating crucible  6  to a growth temperature is disposed in operative relation to chamber  16 , which desirably is water-cooled. Heating means can be realized in any suitable and/or desirable manner, such as RF coil  12 , or a resistive heater or RF coil (not shown) located inside chamber  16 . 
     In order to initiate sublimation growth, crucible  6  is heated by the heating means to a growth temperature, desirably between 2000° C. and 2400° C., in the presence of an inert gas  22 , such as argon or helium gas, inside crucible  4  at a pressure between 1-200 Torr. Under these conditions, source material  4  sublimes and fills the interior of crucible  6  with vapor including Si, Si 2 C and SiC 2  volatile molecules. During growth of a SiC single crystal  14 , the temperature of source material  4  is kept higher than the temperature of seed crystal  8 . This results in vapor transport in the direction from source material  4  to seed crystal  8 . After reaching seed crystal  8 , the vapors condense thereon causing growth of SiC single crystal  14  on seed crystal  8 . 
     During growth of single crystal  14 , inert gas  22  is supplied to growth crucible  4  by passing first through an inlet  24  of chamber  16 . Inert gas  22  inside chamber  20  permeates through the material comprising growth crucible  4  into the interior thereof. 
     After establishing proper conditions for the growth of SiC single crystal  14  inside growth crucible  4 , a valve  26  connected to a nitrogen gas source  28  is opened for a predetermined time interval, desirably between 1 minute and 1 hour. Opening valve  26  enables a predetermined amount of nitrogen to enter chamber  16  and, hence, growth crucible  6 . Graphite has a high permeability to gases, such as argon, helium and nitrogen. Therefore, upon opening valve  26 , nitrogen appears at the crystal growth interface almost immediately. A mass flow controller (MFC) (not shown) can be used to control the pressure of gas inside chamber  16  and, hence, growth crucible  6  to avoid inadvertent changes in this pressure in response to the addition and subtraction of nitrogen to and from the flow of inert gas  22  into chamber  16 . 
     Nitrogen is a known donor in SiC that causes: an increase in the electrical conductivity of SiC; a visible change in the crystal color to green; and a slight change in the lattice parameter. 
     After closing valve  26 , the growth of SiC single crystal  14  continues in the presence of a flow of 1-200 Torr of inert gas  22  in growth crucible  6 , as in a conventional growth process. Upon closing valve  26 , the nitrogen remaining in chamber  16  and growth crucible  6  is quickly removed by the flow of inert gas  22  which is introduced into chamber  16  via inlet  24  and which exits chamber  16  via outlet  30 . 
     After a suitable time interval, e.g., several hours, of undisturbed growth in the presence of a flow of inert gas  22 , valve  26  is opened again for the same or another predetermined time interval, whereupon nitrogen flows into chamber  16  and, hence, into growth crucible  6  again. The foregoing step-wise nitrogen doping cycle is repeated multiple times during the growth of SiC single crystal  14 . 
     A method of PVT growth of a SiC single crystal by intermittently introducing nitrogen into growth crucible  6  is shown in the flowchart of  FIG. 5 , wherein the method commences by advancing from start step  40  to step  42  where PVT growth of a SiC single crystal in a growth atmosphere of between 1 to 200 Torr of a flow of argon or helium gas occurs. 
     The method then advances to step  44  wherein nitrogen is introduced into the growth atmosphere. It is envisioned that at the commencement of the SiC single crystal growth process, steps  42  and  44  can be carried out at the same time, whereupon the initial growth atmosphere can include the combination of nitrogen and argon or helium. Alternatively, the initial growth of the SiC single crystal can occur in a growth atmosphere of only argon or helium and, at a suitable time after the commencement of the SiC single crystal growth, nitrogen can be introduced into the growth atmosphere. 
     The method then advances to step  46  wherein the introduction of nitrogen into the growth atmosphere is terminated. 
     In step  48 , a determination is made whether the growth of the SiC single crystal is complete. If so, the method advances to stop step  50 . Otherwise, the method returns to step  42 . 
     Steps  42 - 48  are then repeated any suitable and/or desirable number of times until, in an iteration of step  48 , it is determined that the growth of SiC single crystal is complete, whereupon the method advances to stop step  50 . 
     In the method, the introduction of nitrogen into the growth atmosphere can occur at periodic intervals (at regular intervals) or at random intervals (at irregular intervals) as deemed suitable and/or desirable by one of ordinary skill in the art. In addition, each interval of crystal growth in the presence of nitrogen can be the same duration or a different duration than any other interval of crystal growth in the presence of nitrogen. Similarly, each interval of crystal growth in the absence of nitrogen in the growth atmosphere can be the same duration or a different duration than any other interval of crystal growth in the absence of nitrogen in the atmosphere. 
     SiC single crystal growth runs were performed in accordance with the above described embodiment. In one growth run, a 6H—SiC single crystal Boule was grown in an atmosphere of pure helium at 30 Torr. The seed crystal and source material temperatures were at 2090° C. and 2130° C., respectively. During growth of the single crystal, the interface was perturbed by admitting nitrogen into the growth atmosphere and simultaneously increasing the total gas pressure in the chamber from 30 Torr to 50 Torr. This step-wise perturbation was repeated twice. 
     In a second growth run, a 6H—SiC single crystal Boule was grown in a growth atmosphere in which nitrogen gas was intermittently introduced. Specifically, the Boule was grown at a seed crystal temperature of 2140° C. and a source material temperature of 2190° C. in a helium ambient of 10 Torr at a flow rate of 248 standard cubic centimeters per minute (sccm). The seed crystal was approximately 1.5 millimeters thick. The source was polycrystalline SiC powder. During a 200 hour growth run, nitrogen pulses of 5 sccm and one minute duration were introduced into the growth atmosphere approximately every 20 hours. Cross sections of the Boule were prepared and studied under a microscope.  FIG. 6  is a photograph of the Boule cross section. The photograph shows two horizontal lines, which correspond to the times when nitrogen was introduced into the growth atmosphere. In this run, a total of 10 “pulses” of nitrogen were periodically or intermittently introduced into the growth atmosphere. Wafers from this Boule were sliced and etched in molten KOH. Etched wafers number  2  and number  17  were examined under a microscope. Photographs of wafers numbers  2  and  17  as viewed under the microscope are shown in  FIGS. 7A and 7B , respectively. As can be seen, wafer number  17  has a significantly reduced dislocation density as compared to wafer number  2 . It should be recognized that wafer number  2  is at the beginning of the Boule growth, whereas wafer number  17  is near the end of the Boule growth. Although it is difficult to ascertain the nature of the dislocations associated with the etch pits shown in wafers numbers  2  and  17 , a close inspection reveals that a vast majority of them are of the threading type, i.e., either TSD or TED. This is not unexpected because the Boule was sliced parallel to its c-axis, and very few of the BPD&#39;s would be visible. Therefore, the observed reduction in etched pit density indicated a reduction in TSD and/or TED. 
     In summary, disclosed herein is a SiC sublimation crystal growth process in which the growth is periodically or intermittently perturbed by step-wise periodic change in the growth conditions. Also disclosed is a SiC sublimation crystal growth process in which the periodic or r intermittent perturbation of growth is caused by a step-wise change in doping level. Desirably, the growth atmosphere is an inert gas, such as argon or helium, and the dopant is a gas or vapor, desirably nitrogen gas. The growth atmosphere can also be a mixture of inert gas with hydrogen. 
     Also or alternatively to perturbation by the introduction of nitrogen into growth crucible  6 , perturbation can also be accomplished by changing the pressure inside growth crucible  6  and/or by changing the temperature inside growth crucible  6 . For example, after establishing suitable conditions for growth of the SiC single crystal  14  inside crucible  6 , perturbation in the growth condition(s) can be caused by increasing and/or decreasing the temperature inside crucible  6  by no more than 100° C., desirably, between 10° C. and 50° C., and more desirably between 25° C. and 50° C. Perturbation by increasing and/or decreasing the temperature during the perturbation interval and then returning the temperature to its starting temperature can occur a plurality of regular and/or irregular intervals of time during the growth of SiC single crystal  14  in crucible  6 . The duration of each perturbation interval can be the same or different. 
     Also or alternatively, after establishing proper conditions for the growth of SiC single crystal  14  inside crucible  6 , perturbation in the growth condition(s) can be caused by increasing or reducing the pressure inside crucible  6  by not more than 100 Torr, desirably between 2 Torr and 50 Torr, and more desirably between 5 Torr and 20 Torr. Perturbation by increasing and/or reducing the pressure inside crucible  6  and then returning the pressure inside crucible  6  to its starting condition can occur a plurality of regular and/or irregular intervals of time during the growth of SiC single crystal  14  in crucible  6 . The duration of each perturbation interval can be the same or different. 
     Heretofore, perturbation of the growth conditions by changing the growth atmosphere, the growth pressure or the growth temperature inside growth crucible  6  were described separately. However, perturbation of the growth conditions can be accomplished by changing any two or more of the atmosphere, the pressure and/or the temperature inside growth crucible  6  during the growth of SiC single crystal  14 . For example, without limitation, when growth pressure is reduced, the temperatures of seed crystal  8  and source material  4  will increase correspondingly if a constant power is maintained to the heating means. Similarly, increasing the temperature inside crucible  6  will cause the pressure inside crucible  6  to increase. Thus, one of the parameters (temperature and pressure) may be adjusted deliberately while the other is allowed to change naturally. Alternatively, the temperature may be adjusted while the pressure is held constant. Still further, both temperature and pressure may be adjusted in concert to achieve perturbation. Accordingly, accomplishing perturbation by changing any one or more of the atmosphere, the pressure and/or the temperature inside crucible  6  is envisioned. 
     As can be seen, perturbation growth of a SiC single crystal by PVT will lead to reduced dislocation density and improved crystal quality of the SiC single crystal substrate, especially with regard to 4H—SiC substrates used for power-switching semiconductor devices. 
     The invention has been described with reference to the preferred embodiment. Obvious modifications and alterations will occur to others upon reading and understanding the preceding detailed description. It is intended that the invention be construed as including all such modifications and alterations insofar as they come within the scope of the appended claims or the equivalents thereof.