Abstract:
A semiconductor device and method are being disclosed. The semiconductor device discloses an InAs layer, a plurality of group III-V ternary layers supported by the InAs layer, and a plurality of group III-V quarternary layers supported by the InAs layer, wherein the group III-V ternary layers are separated from each other by a single group III-V quarternary layer. The method discloses providing an InAs layer, growing a plurality of group III-V ternary layers, and growing a plurality of group III-V quarternary layers, wherein the group III-V ternary layers are separated from each other by a single group III-V quarternary layer and are supported by the InAs layer.

Description:
CROSS-REFERENCE TO RELATED APPLICATIONS 
     This is a divisional application of U.S. patent application Ser. No. 12/491,004, filed on Jun. 24, 2009, which is incorporated herein as though set forth in full. U.S. patent application Ser. No. 12/491,004 is a division of U.S. patent application Ser. No. 11/447,338, filed on Jun. 5, 2006, the disclosure of which is incorporated herein by reference. 
    
    
     FIELD 
     This disclosure relates to materials that mimic the properties of an AlInAsSb quaternary and are lattice matched to InAs. 
     BACKGROUND AND PRIOR ART 
     The growth of AlInAsSb has not been extensively studied, perhaps because of the large miscibility gap predicted for these alloys. See K. Onabe, NEC Res. Dev. 72, 1 (1984). 
     Groups at the University of Houston/University of North Texas (D. Washington, T. Hogan, P. Chow, T. Golding, C. Littler, and U. Kirschbaum, J. Vac. Sci. Technol. B16, 1385 (1998); R. Lukic-Zrnic, D. W. Stokes, C. L. Littler, and T. D. Golding, Semicond. Sci. Technol. 16, 353 (2001)) and HRL LABS (D. H. Chow, Y. H. Zhang, R. H. Miles, and H. L. Dunlap, J. Cryst. Growth 150, 879 (1995)) examined AlInAsSb lattice-matched to GaSb substrates. The Texas group controlled the quaternary composition by adjusting the Al:In and As:Sb flux ratios, while the HRL LABS group grew superlattices of the binary materials InAs and AlSb. 
     A group at U.C.S.B (S. K. Mathis, K. H. A. Lau, A. M Andrews, E. M. Hall, G. Almuneau, E. L. Hu, and J. S. Speck, J. Appl. Phys. 89, 2458 (2001)) examined AlInAsSb alloys lattice-matched to InP substrates. As with the Texas group, quaternary composition was controlled by adjusting the Al:In and As:Sb flux ratios. 
     Finally, groups at Lincoln Lab/MIT (G. W. Turner, M. J. Manfra, H. K. Choi, and M. K. Connors, J. Cryst. Growth 175/176, 825 (1997)) and Université de Montpellier II (A. Wilk, B. Fraisse, P. Christol, G. Boissier, P. Grech, M. El Gazouli, Y. Rouillard, A. N. Baranov, and A. Joullié, J. Cryst. Growth 227/228, 586 (2001)) examined AlInAsSb alloys on InAs substrates. Both of these groups also controlled the quaternary composition by adjusting the Al:In and As:Sb flux ratios. The Lincoln Lab/MIT group grew a tensile-strained alloy, while the Montpellier group studied a lattice-matched alloy, but both groups incorporated relatively small Al mole fractions (15% and 12%, respectively). 
     Rather than grow the AlInAsSb quaternary directly, as most groups have done, or as a digital binary superlattice, a technique of growing a ternary/quaternary superlattice is disclosed presently. The overall composition may be controlled by adjusting the As:Sb flux ratio and by modulating the Sb beam. 
     The disclosed technique may allow access to a wider range of quaternary compositions than may be possible with a digital binary superlattice. 
     The disclosed technique may further be applicable to manufacturing electronic and optoelectronic devices such as, for example, InAs-channel HEMTs, InAs HBTs, and laser diodes which may require semiconductor materials that are lattice-matched to InAs. 
     The growth of alloys according to the disclosed technique may also impose an artificial, short-period order, which may frustrate the tendency of the film to dissociate into more stable components. 
    
    
     
       BRIEF DESCRIPTION OF THE FIGURES 
         FIG. 1  depicts an exemplary molecular beam epitaxy device; 
         FIG. 2  depicts a summary of x-ray diffraction data according to the present disclosure; 
         FIGS. 3A-3B  depict an exemplary superlattice  240  as shown in  FIG. 2 ; 
         FIGS. 4A-4B  depict exemplary superlattice  250  as shown in  FIG. 2 ; 
         FIGS. 5A-5B  depict exemplary superlattice  260  as shown in  FIG. 2 ; and 
         FIGS. 6A-6B  depict another exemplary superlattice. 
     
    
    
     DETAILED DESCRIPTION 
     In the following description, like reference numbers are used to identify like elements. Furthermore, the drawings are intended to illustrate major features of exemplary embodiments in a diagrammatic manner. The drawings are not intended to depict every feature of every implementation nor relative dimensions of the depicted elements, and are not drawn to scale. 
     A technique for growing pseudo-random AlInAsSb quaternary alloys lattice-matched to InAs is disclosed presently. The disclosed technique implements short-period Group III-V materials in a superlattice to mimic the properties of random AlInAsSb quaternaries, wherein Group III-V superlattice may contain ternary/quaternary materials such as AlInAs/AlInAsSb. 
     Referring to  FIG. 1 , a molecular beam epitaxy device  100  may, for example, be used to form the Group III-V superlattice on an InAs substrate  130 . For clarity a simplified version of molecular beam epitaxy device  100  is shown in  FIG. 1 . Molecular beam epitaxy devices are well known in the art and the type of device that could be utilized to implement the disclosed method and system is not limited to the particular device disclosed herein. Molecular beam epitaxy device  100  may contain material sources  110  for emitting materials to be deposited on the InAs substrate  130 . Each of the material sources  110  may, for example, contain either Al, In, As, or Sb materials. Each material source  110  may be opened and closed by using a shutter  120  associated with each material source  110 . Layers of material may be formed on the InAs substrate  130  by emitting material from one or more of the material sources  110 . The thickness of each layer may be determined by the amount of time the shutter  120  for each material source  110  may be open. The composition of each layer may be determined by the combination of shutters  120  that are opened at the same time. 
     Molecular beam epitaxy device  100  may be used to grow a ternary/quaternary superlattice out of, for example, AlInAs/AlInAsSb materials, that may not be lattice matched to the InAs substrate  130 . The overall composition of the AlInAs/AlInAsSb superlattice, which may mimic an AlInAsSb quaternary material, may be controlled by varying the ratio of the thicknesses of the constituent layers and the As:Sb flux ratio. In practice, the thicknesses of each layer within the AlInAs/AlInAsSb superlattice and the As:Sb flux ratio may be controlled by varying the fraction of time the shutter  120 , that is associated with material sources  110  containing Sb material, may be open and by varying the temperature of the material sources  110  containing Sb material. 
     Group III-V superlattice formed on the InAs substrate  130  may be characterized in situ using reflection high-energy electron diffraction or ex situ using x-ray diffraction and optical inspection.  FIG. 2  depicts a summary of the x-ray diffraction data for exemplary Group III-V superlattices  240 ,  250 ,  260  that may be formed wherein each of the superlattices  240 ,  250 ,  260  represents a different growth. As represented in  FIG. 2 , the superlattice  250  is under tensile strain, the superlattice  260  is under a compression strain and the superlattice  240  is lattice matched to the InAs substrate  130 . Referring to  FIG. 2 , the x-axis represents units of degrees θ and the y-axis represents the x-ray intensity. 
     Referring to  FIG. 2 , based on the x-ray diffraction data, the exemplary superlattice  240 , containing Al mole fraction of 15%, appears to be lattice matched to the InAs substrate  130 , whereas the lattice parameters of the exemplary superlattices  250 ,  260 , containing Al mole fraction of 22%, do not appear to be lattice matched to the InAs substrate  130 . Increasing the mole fraction of Al may increase a bandgap of a structure which may be desirable for electronic and optoelectronic devices. So, in order to achieve a lattice match between a superlattice containing Al mole fraction of 22% and InAs substrate  130 , an appropriate time may be chosen that the shutter  120  associated with material sources  110  containing Sb material, may be open. 
     Referring to  FIGS. 2 ,  3 A and  3 B, an exemplary superlattice  240 , composed of ternary/quaternary materials such as Al 0.15 In 0.85 AsSb/Al 0.15 In 0.85 As, may be formed to be lattice matched to the InAs substrate  130 . 
     Referring to  FIG. 3A , in one exemplary embodiment, an initial ternary monolayer  301  of AlInAs material may be formed on the InAs substrate  130  followed by formation of a quaternary layer  302  of AlInAsSb material. In this exemplary embodiment, one sub-superlattice  305  may be composed of one quaternary layer  302  of about 12 Angstroms in thickness and one ternary monolayer  301  of about 3 Angstroms in thickness. The process of forming sub-superlattices  305  may be repeated until the superlattice  240  is formed. 
     Referring to  FIG. 3B , in another exemplary embodiment, a quaternary layers  302  of AlInAsSb material may be formed on the InAs substrate  130  followed by formation of a ternary monolayer  301  of AlInAs material. In this exemplary embodiment, one sub-superlattice  306  may be composed of one quaternary layers  302  of about 12 Angstroms in thickness and one ternary monolayer  301  of about 3 Angstroms in thickness. As above, the process of forming sub-superlattices  306  once again may be repeated until the superlattice  240  may be formed. 
     Referring to  FIGS. 2 ,  4 A and  4 B, an exemplary superlattice  250 , composed of ternary/quaternary materials such as Al 0.22 In 0.78 AsSb/Al 0.22 In 0.78 As, may be formed to be coherently strained (no dislocations) on the InAs substrate  130 . 
     Referring to  FIG. 4A , in one exemplary embodiment, an initial ternary monolayer  401  of AlInAs material may be formed on the InAs substrate  130  followed by formation of a quaternary layers  402  of AlInAsSb material. In this exemplary embodiment, one sub-superlattice  405  may be composed of one quaternary layer  402  of about 12 Angstroms in thickness and one ternary monolayer  401  of about 3 Angstroms in thickness. The process of forming sub-superlattices  405  may be repeated until the superlattice  250  is formed. 
     Referring to  FIG. 4B , in another exemplary embodiment, a quaternary layer  402  of AlInAsSb material may be formed on the InAs substrate  130  followed by formation of a ternary monolayer  401  of AlInAs material. In this exemplary embodiment, one sub-superlattice  406  may be composed of one quaternary layer  402  of about 12 Angstroms in thickness and one ternary monolayer  401  of about 3 Angstroms in thickness. As above, the process of forming sub-superlattices  406  once again may be repeated until the superlattice  250  is formed. 
     Referring to  FIGS. 2 ,  5 A and  5 B, an exemplary superlattice  260 , composed of ternary/quaternary materials such as Al 0.22 In 0.78 AsSb/Al 0.22 In 0.78 As, may be formed to be coherently strained (no dislocations) on the InAs substrate  130 . 
     Referring to  FIG. 5A , in one exemplary embodiment, an initial ternary monolayer  501  of AlInAs material may be formed on the InAs substrate  130  followed by formation of a quaternary layer  502  of AlInAsSb material. In this exemplary embodiment, one sub-superlattice  505  may be composed of one quaternary layer  502  of about 18 Angstroms in thickness and one ternary monolayer  501  of about 3 Angstroms in thickness. The process of forming sub-superlattices  505  may be repeated until the superlattice  260  is formed. 
     Referring to  FIG. 5B , in another exemplary embodiment, a quaternary layer  502  of AlInAsSb material may be formed on the InAs substrate  130  followed by formation of a ternary monolayer  501  of AlInAs material. In this exemplary embodiment, one sub-superlattice  506  may be composed of one quaternary layer  502  of about 18 Angstroms in thickness and one ternary monolayer  501  of about 3 Angstroms in thickness. As above, the process of forming sub-superlattices  506  once again may be repeated until the superlattice  260  is formed. 
     Referring to  FIGS. 6A and 6B , an exemplary superlattice  270 , composed of ternary/quaternary materials such as Al 0.22 In 0.78 AsSb/Al 0.22 In 0.78 As, may be formed to be lattice matched to the InAs substrate  130 . Wherein mole fraction of Al may be about 22%. Once again, increasing the mole fraction of Al increases a bandgap of the exemplary superlattice  270  which may be desirable for electronic and optoelectronic devices. 
     Referring to  FIG. 6A , in one exemplary embodiment, an initial ternary monolayer  601  of AlInAs material may be formed on the InAs substrate  130  followed by formation of a quaternary layer  602  of AlInAsSb material. In this exemplary embodiment, one sub-superlattice  605  may be composed of one quaternary layer  602  of about 15 Angstroms in thickness and one ternary monolayer  601  of about 3 Angstroms in thickness. The process of forming sub-superlattices  605  may be repeated until the superlattice  270  is formed. 
     Referring to  FIG. 6B , in another exemplary embodiment, a quaternary layer  602  of AlInAsSb material may be formed on the InAs substrate  130  followed by formation of a ternary monolayer  601  of AlInAs material. In this exemplary embodiment, one sub-superlattice  606  may be composed of one quaternary layer  602  of about 15 Angstroms in thickness and one ternary monolayer  601  of about 3 Angstroms in thickness. As above, the process of forming sub-superlattices  606  once again may be repeated until the superlattice  270  is formed. 
     The above disclosed techniques may be applicable to manufacturing electronic and optoelectronic devices such as, for example, InAs-channel HEMTs, InAs HBTs, and laser diodes which may require semiconductor materials that are lattice-matched to InAs. As known in the art, the defining characteristic of a semiconductor is the existence of a forbidden energy gap between the top of the valence band and the bottom of the conduction band. This energy gap is called a bandgap. Many electronic devices take advantage of the favorable electronic properties that result when a material with a relatively large bandgap (a.k.a. wide bandgap) is brought into contact with a material with a relatively small bandgap (a.k.a. narrow bandgap). This may be achieved, for example, by growing the wide bandgap material on top of the narrow bandgap material, or vice versa, by molecular beam epitaxy or by some other material growth technique. Relevant devices include:
         1. Heterojunction bipolar transistors (HBTs), in which the emitter layer (or the collector layer) has a bandgap wider than that of the base layer.   2. High electron mobility transistors (HEMTs), in which the Schottky layer has a bandgap wider than that of the channel layer.   3. Semiconductor lasers, in which the inactive confinement or cladding layers have a bandgap wider than that of the active layer.       

     According to the present disclosure, AlInAsSb alloys disclosed above have lattice parameters equal to that of InAs material and have bandgaps that are greater than that of InAs material. Thus, the present disclosure enables the construction of, for example:
         1. HBTs with AlInAsSb emitter layers (and also collector layers) and InAs base layers.   2. HEMTs with AlInAsSb Schottky layers and InAs channel layers.   3. Semiconductor lasers with AlInAsSb confinement and cladding layers and InAs active layers.       

     The foregoing Detailed Description of exemplary and preferred embodiments is presented for purposes of illustration and disclosure in accordance with the requirements of the law. It is not intended to be exhaustive nor to limit the invention to the precise form(s) described, but only to enable others skilled in the art to understand how the invention may be suited for a particular use or implementation. The possibility of modifications and variations will be apparent to practitioners skilled in the art. No limitation is intended by the description of exemplary embodiments which may have included tolerances, feature dimensions, specific operating conditions, engineering specifications, or the like, and which may vary between implementations or with changes to the state of the art, and no limitation should be implied therefrom. Applicant has made this disclosure with respect to the current state of the art, but also contemplates advancements and that adaptations in the future may take into consideration of those advancements, namely in accordance with the then current state of the art. It is intended that the scope of the invention be defined by the Claims as written and equivalents as applicable. Reference to a claim element in the singular is not intended to mean “one and only one” unless explicitly so stated. Moreover, no element, component, nor method or process step in this disclosure is intended to be dedicated to the public regardless of whether the element, component, or step is explicitly recited in the Claims. No claim element herein is to be construed under the provisions of 35 U.S.C. Sec. 112, sixth paragraph, unless the element is expressly recited using the phrase “means for . . . ” and no method or process step herein is to be construed under those provisions unless the step, or steps, are expressly recited using the phrase “step(s) for . . . .”