Patent Publication Number: US-8524618-B2

Title: Hafnium tantalum oxide dielectrics

Description:
This application is a Continuation of U.S. application Ser. No. 12/577,624, filed on Oct. 12, 2009, which is a Continuation of U.S. application Ser. No. 11/735,247, filed Apr. 13, 2007, now issued as U.S. Pat. No. 7,602,030, which is a divisional of U.S. application Ser. No. 11/029,757 filed Jan. 5, 2005, now issued as U.S. Pat. No. 7,560,395, which are incorporated herein by reference in their entirety. 
    
    
     TECHNICAL FIELD 
     This application relates generally to semiconductor devices and device fabrication and, more particularly, to dielectric layers and their method of fabrication. 
     BACKGROUND 
     The semiconductor device industry has a market driven need to reduce the size of devices such as transistors. To reduce transistor size, the thickness of the silicon dioxide, SiO 2 , gate dielectric is reduced in proportion to the shrinkage of the gate length. For example, a metal-oxide-semiconductor field effect transistor (MOSFET) would use a 1.5 nm thick SiO 2  gate dielectric for a gate length of 70 nm. A goal is to fabricate increasingly smaller and more reliable integrated circuits (ICs) for use in products such as processor chips, mobile telephones, and memory devices such as dynamic random access memories (DRAMs). 
     Currently, the semiconductor industry relies on the ability to reduce or scale the dimensions of its basic devices, primarily, the silicon based MOSFET type devices. This device scaling includes scaling the gate dielectric, which has primarily been fabricated using silicon dioxide. A thermally grown amorphous SiO 2  layer provides an electrically and thermodynamically stable material, where the interface of the SiO 2  layer with underlying silicon provides a high quality interface as well as superior electrical isolation properties. However, increased scaling and other requirements in microelectronic devices have created the need to use other dielectric materials as gate dielectrics. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  depicts an atomic layer deposition system for fabricating a dielectric layer containing a hafnium tantalum oxide layer, according to various embodiments. 
         FIG. 2  illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a hafnium tantalum oxide layer by atomic layer deposition. 
         FIG. 3  illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a hafnium tantalum oxide layer by atomic layer deposition. 
         FIG. 4  shows an embodiment of a configuration of a transistor having a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. 
         FIG. 5  shows an embodiment of a configuration of a floating gate transistor having a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. 
         FIG. 6  shows an embodiment of a configuration of a capacitor having a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. 
         FIG. 7  depicts an embodiment of a dielectric layer including a nanolaminate having at least one layer containing an atomic layer deposited hafnium tantalum oxide layer. 
         FIG. 8  is a simplified diagram for an embodiment of a controller coupled to an electronic device, in which at least one of the two includes a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. 
         FIG. 9  illustrates a diagram for an embodiment of an electronic system having devices with a dielectric film containing an atomic layer deposited hafnium tantalum oxide layer. 
     
    
    
     DETAILED DESCRIPTION 
     The following detailed description refers to the accompanying drawings that show, by way of illustration, specific aspects and embodiments in which the present invention may be practiced. These embodiments are described in sufficient detail to enable those skilled in the art to practice the present invention. Other embodiments may be utilized and structural, logical, and electrical changes may be made without departing from the scope of the present invention. The various embodiments disclosed herein are not necessarily mutually exclusive, as some disclosed embodiments can be combined with one or more other disclosed embodiments to form new embodiments. 
     The terms wafer and substrate used in the following description include any structure having an exposed surface with which to form an integrated circuit (IC) structure. The term substrate is understood to include semiconductor wafers. The term substrate is also used to refer to semiconductor structures during processing, and may include other layers that have been fabricated thereupon. Both wafer and substrate include doped and undoped semiconductors, epitaxial semiconductor layers supported by a base semiconductor or insulator, as well as other semiconductor structures well known to one skilled in the art. The term conductor is understood to generally include n-type and p-type semiconductors and the term insulator or dielectric is defined to include any material that is less electrically conductive than the materials referred to as conductors or as semiconductors. The following detailed description is, therefore, not to be taken in a limiting sense, and the scope of the present invention is defined only by the appended claims, along with the full scope of equivalents to which such claims are entitled. 
     A gate dielectric in a transistor has both a physical gate dielectric thickness and an equivalent oxide thickness (t eq ). The equivalent oxide thickness quantifies the electrical properties, such as capacitance, of the gate dielectric in terms of a representative physical thickness. t eq  is defined as the thickness of a theoretical SiO 2  layer that would be required to have the same capacitance density as a given dielectric, ignoring leakage current and reliability considerations. 
     A SiO 2  layer of thickness, t, deposited on a Si surface as a gate dielectric will have a t eq  larger than its thickness, t. This t eq  results from the capacitance in the surface channel on which the SiO 2  is deposited due to the formation of a depletion/inversion region. This depletion/inversion region can result in t eq  being from 3 to 6 Angstroms (Å) larger than the SiO 2  thickness, t. Thus, with the semiconductor industry driving to someday scale the gate dielectric equivalent oxide thickness to under 10 Å, the physical thickness for a SiO 2  layer used for a gate dielectric would be need to be approximately 4 to 7 Å. 
     Additional requirements on a SiO 2  layer would depend on the gate electrode used in conjunction with the SiO 2  gate dielectric. Using a conventional polysilicon gate would result in an additional increase in t eq  for the SiO 2  layer. This additional thickness could be eliminated by using a metal gate electrode, though metal gates are not currently used in typical complementary metal-oxide-semiconductor field effect transistor (CMOS) technology. Thus, future devices would be designed towards a physical SiO 2  gate dielectric layer of about 5 Å or less. Such a small thickness for a SiO 2  oxide layer creates additional problems. 
     Silicon dioxide is used as a gate dielectric, in part, due to its electrical isolation properties in a SiO 2 —Si based structure. This electrical isolation is due to the relatively large band gap of SiO 2  (8.9 eV) making it a good insulator from electrical conduction. Signification reductions in its band gap would eliminate it as a material for a gate dielectric. As the thickness of a SiO 2  layer decreases, the number of atomic layers, or monolayers of the material in the thickness decreases. At a certain thickness, the number of monolayers will be sufficiently small that the SiO 2  layer will not have a complete arrangement of atoms as in a larger or bulk layer. As a result of incomplete formation relative to a bulk structure, a thin SiO 2  layer of only one or two monolayers will not form a full band gap. The lack of a full band gap in a SiO 2  gate dielectric may cause an effective short between an underlying Si channel and an overlying polysilicon gate. This undesirable property sets a limit on the physical thickness to which a SiO 2  layer can be scaled. The minimum thickness due to this monolayer effect is thought to be about 7-8 Å. Therefore, for future devices to have a t eq  less than about 10 Å, other dielectrics than SiO 2  need to be considered for use as a gate dielectric. 
     For a typical dielectric layer used as a gate dielectric, the capacitance is determined as one for a parallel plate capacitance: C=κ∈ 0 A/t, where κ is the dielectric constant, ∈ 0  is the permittivity of free space, A is the area of the capacitor, and t is the thickness of the dielectric. The thickness, t, of a material is related to its t eq  for a given capacitance, with SiO 2  having a dielectric constant κ ox =3.9, as
 
 t =(κ/κ ox ) t   eq =(κ/3.9) t   eq .
 
Thus, materials with a dielectric constant greater than that of SiO 2 , 3.9, will have a physical thickness that can be considerably larger than a desired t eq , while providing the desired equivalent oxide thickness. For example, an alternate dielectric material with a dielectric constant of 10 could have a thickness of about 25.6 Å to provide a t eq  of 10 Å, not including any depletion/inversion layer effects. Thus, a reduced equivalent oxide thickness for transistors can be realized by using dielectric materials with higher dielectric constants than SiO 2 .
 
     The thinner equivalent oxide thickness required for lower transistor operating voltages and smaller transistor dimensions may be realized by a significant number of materials, but additional fabricating requirements makes determining a suitable replacement for SiO 2  difficult. The current view for the microelectronics industry is still for Si based devices. This requires that the gate dielectric employed be grown on a silicon substrate or silicon layer, which places significant constraints on the substitute dielectric material. During the formation of the dielectric on the silicon layer, a small layer of SiO 2  may be formed in addition to the desired dielectric. The result would effectively be a dielectric layer consisting of two sublayers in parallel with each other and the silicon layer on which the dielectric is formed. In such a case, the resulting capacitance would be that of two dielectrics in series. As a result, the t eq  of the dielectric layer would be the sum of the SiO 2  thickness and a multiplicative factor of the thickness, t, of the dielectric being formed, written as
 
 t   eq   =t   SiO     2   +(κ ox /κ) t.  
 
Thus, if a SiO 2  layer is formed in the process, the t eq  is again limited by a SiO 2  layer. In the event that a barrier layer is formed between the silicon layer and the desired dielectric in which the barrier layer prevents the formation of a SiO 2  layer, the t eq  would be limited by the layer with the lowest dielectric constant. However, whether a single dielectric layer with a high dielectric constant or a barrier layer with a higher dielectric constant than SiO 2  is employed, the layer interfacing with the silicon layer must provide a high quality interface to maintain a high channel carrier mobility.
 
     One of the advantages in using SiO 2  as a gate dielectric has been that the formation of the SiO 2  layer results in an amorphous gate dielectric. Having an amorphous structure for a gate dielectric provides for reducing problems of leakage current associated with grain boundaries in polycrystalline gate dielectrics that provide high leakage paths. Additionally, grain size and orientation changes throughout a polycrystalline gate dielectric can cause variations in the film&#39;s dielectric constant, along with uniformity and surface topography problems. Typically, materials having the advantage of a high dielectric constant relative to SiO 2  also have the disadvantage of a crystalline form, at least in a bulk configuration. The best candidates for replacing SiO 2  as a gate dielectric are those with high dielectric constant, which can be fabricated as a thin layer with an amorphous form. 
     Candidates to replace SiO 2  include high-κ dielectric materials. High-κ materials include materials having a dielectric constant greater than silicon dioxide, for example, dielectric materials having a dielectric constant greater than about twice the dielectric constant of silicon dioxide. Examples of such high-κ materials include Ta 2 O 3 , TiO 2 , Al 2 O 3 , ZrO 2 , HfO 2 , Y 2 O 3 , ZrSi x O y , HfSi x O y , HfSiON, and barium strontium titanate (BST). An appropriate high-κ gate dielectric to replace SiO 2  should have a large energy gap (E g ) and large energy barrier heights with Si for both electrons and holes. Generally, the bandgap is inversely related to the dielectric constant for a high-κ material, which lessens some advantages of the high-κ material. Further, for integration into conventional CMOS processes, mobility degradation and electrical stability for high-κ materials may need to be considered. 
     Other characteristics for choosing a silicon oxide replacement include using materials that provide a sharp interface with silicon that may provide a low density of interface states, a large energy barrier from the conduction band to the Fermi level of the gate electrode to maintain leakage current at acceptable levels, and structural stability with contact electrodes and substrate material during device processing steps performed after providing the dielectric layer. 
     Embodiments for forming a hafnium tantalum oxide film by atomic layer deposition may provide a film having a specific stoichiometry or it may be a non-stoichiometric hafnium tantalum oxide. The expression Hf x Ta y O z  is used herein to represent a non-stoichiometric and/or a stoichiometric hafnium tantalum oxide. Embodiments of dielectric layers containing an atomic layer deposited hafnium tantalum oxide layer have a larger dielectric constant than silicon dioxide. Such dielectric layers provide a significantly thinner equivalent oxide thickness compared with a silicon oxide layer having the same physical thickness. Alternately, such dielectric layers provide a significantly thicker physical thickness than a silicon oxide layer having the same equivalent oxide thickness. This increased physical thickness aids in reducing leakage current. 
     Another consideration for selecting the material and method for forming a dielectric layer for use in electronic devices and systems concerns the roughness of a dielectric layer on a substrate. Surface roughness of the dielectric layer has a significant effect on the electrical properties of the gate oxide, and the resulting operating characteristics of the transistor. The leakage current through a physical 1.0 nm gate oxide increases by a factor of 10 for every 0.1 increase in the root-mean-square (RMS) roughness. 
     During a conventional sputtering deposition process stage, particles of the material to be deposited bombard the surface at a high energy. When a particle hits the surface, some particles adhere, and other particles cause damage. High energy impacts remove body region particles, creating pits. The surface of such a deposited layer can have a rough contour due to the rough interface at the body region. 
     In an embodiment, a hafnium tantalum oxide dielectric layer having a substantially smooth surface relative to other processing techniques is formed using atomic layer deposition (ALD). Further, forming such a dielectric layer using atomic layer deposition can provide for controlling transitions between material layers. Thus, atomic layer deposited hafnium tantalum oxide dielectric layers can have an engineered transition with a substrate surface. 
     ALD, also known as atomic layer epitaxy (ALE), is a modification of chemical vapor deposition (CVD) and is also called “alternatively pulsed-CVD.” In ALD, gaseous precursors are introduced one at a time to the substrate surface mounted within a reaction chamber (or reactor). This introduction of the gaseous precursors takes the form of pulses of each gaseous precursor. In a pulse of a precursor gas, the precursor gas is made to flow into a specific area or region for a short period of time. Between the pulses, the reaction chamber is purged with a gas, which in many cases is an inert gas, and/or evacuated. 
     In a chemisorption-saturated ALD (CS-ALD) process, during the first pulsing phase, reaction with the substrate occurs with the precursor saturatively chemisorbed at the substrate surface. Subsequent pulsing with a purging gas removes precursor excess from the reaction chamber. 
     The second pulsing phase introduces another precursor on the substrate where the growth reaction of the desired film takes place. Subsequent to the film growth reaction, reaction byproducts and precursor excess are purged from the reaction chamber. With favourable precursor chemistry where the precursors adsorb and react with each other on the substrate aggressively, one ALD cycle can be preformed in less than one second in properly designed flow type reaction chambers. Typically, precursor pulse times range from about 0.5 sec to about 2 to 3 seconds. 
     In ALD, the saturation of all the reaction and purging phases makes the growth self-limiting. This self-limiting growth results in large area uniformity and conformality, which has important applications for such cases as planar substrates, deep trenches, and in the processing of porous silicon and high surface area silica and alumina powders. Significantly, ALD provides for controlling film thickness in a straightforward manner by controlling the number of growth cycles. 
     ALD was originally developed to manufacture luminescent and dielectric layers needed in electroluminescent displays. Significant efforts have been made to apply ALD to the growth of doped zinc sulfide and alkaline earth metal sulfide films. Additionally, ALD has been studied for the growth of different epitaxial II-V and II-VI films, nonepitaxial crystalline or amorphous oxide and nitride films and multilayer structures of these. There also has been considerable interest towards the ALD growth of silicon and germanium films, but due to the difficult precursor chemistry, this has not been very successful. 
     The precursors used in an ALD process may be gaseous, liquid or solid. However, liquid or solid precursors should be volatile. The vapor pressure should be high enough for effective mass transportation. Also, solid and some liquid precursors may need to be heated inside the reaction chamber and introduced through heated tubes to the substrates. The necessary vapor pressure should be reached at a temperature below the substrate temperature to avoid the condensation of the precursors on the substrate. Due to the self-limiting growth mechanisms of ALD, relatively low vapor pressure solid precursors can be used, though evaporation rates may vary somewhat during the process because of changes in their surface area. 
     There are several other characteristics for precursors used in ALD. The precursors should be thermally stable at the substrate temperature because their decomposition would destroy the surface control and accordingly the advantages of the ALD method that relies on the reaction of the precursor at the substrate surface. A slight decomposition, if slow compared to the ALD growth, can be tolerated. 
     The precursors should chemisorb on or react with the surface, though the interaction between the precursor and the surface as well as the mechanism for the adsorption is different for different precursors. The molecules at the substrate surface should react aggressively with the second precursor to form the desired solid film. Additionally, precursors should not react with the film to cause etching, and precursors should not dissolve in the film. Using highly reactive precursors in ALD contrasts with the selection of precursors for conventional CVD. 
     The by-products in the reaction should be gaseous in order to allow their easy removal from the reaction chamber. Further, the by-products should not react or adsorb on the surface. 
     In a reaction sequence ALD (RS-ALD) process, the self-limiting process sequence involves sequential surface chemical reactions. RS-ALD relies on chemistry between a reactive surface and a reactive molecular precursor. In an RS-ALD process, molecular precursors are pulsed into the ALD reaction chamber separately. The metal precursor reaction at the substrate is typically followed by an inert gas pulse to remove excess precursor and by-products from the reaction chamber prior to pulsing the next precursor of the fabrication sequence. 
     By RS-ALD, films can be layered in equal metered sequences that are all identical in chemical kinetics, deposition per cycle, composition, and thickness. RS-ALD sequences generally deposit less than a full layer per cycle. Typically, a deposition or growth rate of about 0.25 to about 2.00 Å per RS-ALD cycle can be realized. 
     The advantages of RS-ALD include continuity at an interface avoiding poorly defined nucleating regions that are typical for chemical vapor deposition (&lt;20 Å) and physical vapor deposition (&lt;50 Å), conformality over a variety of substrate topologies due to its layer-by-layer deposition technique, use of low temperature and mildly oxidizing processes, lack of dependence on the reaction chamber, growth thickness dependent solely on the number of cycles performed, and ability to engineer multilayer laminate films with resolution of one to two monolayers. RS-ALD processes allow for deposition control on the order of monolayers and the ability to deposit monolayers of amorphous films. 
     Herein, a sequence refers to the ALD material formation based on an ALD reaction of one precursor with its reactant precursor. For example, forming tantalum oxide from a TaCl 5  precursor and H 2 O, as its reactant precursor, forms an embodiment of a tantalum/oxygen sequence, which can also be referred to as a tantalum sequence. A cycle of a sequence includes pulsing a precursor, pulsing a purging gas for the precursor, pulsing a reactant precursor, and pulsing the reactant&#39;s purging gas. For an oxide compound containing two or more metals, a cycle may contain a number of sequences corresponding to each metal of the metals in the compound. However, in forming a layer of a metal species, an ALD sequence deals with reacting a precursor containing the metal species with a substrate surface. A cycle for such a metal forming sequence includes pulsing a purging gas after pulsing the precursor containing the metal species. In an embodiment, a layer of hafnium tantalum oxide is formed on a substrate mounted in a reaction chamber using ALD in repetitive tantalum sequences and hafnium sequences, using precursor gases individually pulsed into the reaction chamber. Alternately, solid or liquid precursors can be used in an appropriately designed reaction chamber. 
       FIG. 1  shows an embodiment of an atomic layer deposition system  100  for processing a dielectric film containing hafnium tantalum oxide. The elements depicted permit discussion of various embodiments such that those skilled in the art may practice similar embodiments without undue experimentation. In  FIG. 1 , a substrate  110  is located inside a reaction chamber  120  of ALD system  100 . Also located within the reaction chamber  120  is a heating element  130 , which is thermally coupled to substrate  110  to control the substrate temperature. A gas-distribution fixture  140  introduces precursor gases to the substrate  110 . Each precursor gas originates from individual gas sources  151 - 154 , whose flow is controlled by mass-flow controllers  156 - 159 , respectively. Gas sources  151 - 154  provide a precursor gas either by storing the precursor as a gas or by providing a location and apparatus for evaporating a solid or liquid material to form the selected precursor gas. 
     Also included in the ALD system are purging gas sources  161 ,  162 , each of which is coupled to mass-flow controllers  166 ,  167 , respectively. Furthermore, additional purging gas sources can be constructed in ALD system  100 , one purging gas source for each precursor gas, for example. For a process that uses the same purging gas for multiple precursor gases, fewer purging gas sources are required for ALD system  100 . Gas sources  151 - 154  and purging gas sources  161 - 162  are coupled by their associated mass-flow controllers to a common gas line or conduit  170 , which is coupled to the gas-distribution fixture  140  inside the reaction chamber  120 . Gas conduit  170  is also coupled to vacuum pump, or exhaust pump,  181  by mass-flow controller  186  to remove excess precursor gases, purging gases, and by-product gases at the end of a purging sequence from the gas conduit. 
     Vacuum pump, or exhaust pump,  182  is coupled by mass-flow controller  187  to remove excess precursor gases, purging gases, and by-product gases at the end of a purging sequence from reaction chamber  120 . For convenience, control displays, mounting apparatus, temperature sensing devices, substrate maneuvering apparatus, and necessary electrical connections as are known to those skilled in the art are not shown in  FIG. 1 . Though ALD system  100  is well suited for performing various embodiments, other commercially available ALD systems can be used. 
     The use, construction and fundamental operation of reaction chambers for deposition of films are understood by those of ordinary skill in the art of semiconductor fabrication. Embodiments may be practiced on a variety of such reaction chambers without undue experimentation. Furthermore, one of ordinary skill in the art will comprehend the necessary detection, measurement, and control techniques in the art of semiconductor fabrication upon studying this disclosure. 
     The elements of ALD system  100  can be controlled by a computer. To focus on the use of ALD system  100  in the various embodiments, the computer is not shown. Those skilled in the art can appreciate that the individual elements such as pressure control, temperature control, and gas flow within ALD system  100  can be under computer control. 
       FIG. 2  illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing a hafnium tantalum oxide layer using atomic layer deposition. Such a dielectric layer may be formed as a dielectric layer above a body region and below a gate of an electronic device. At  210 , in an atomic layer deposition process a precursor containing hafnium is pulsed onto a substrate surface to deposit hafnium. The precursor may be an anhydrous hafnium nitrate. Alternatively, a hafnium halide precursor, such as HfCl 4  or HfI 4 , may be pulsed to deposit hafnium on the substrate surface. In addition, the pulsing of the hafnium precursor may use a pulsing period that provides uniform coverage of a monolayer on the surface or may use a pulsing period that provides partial formation of a monolayer on the surface during a hafnium sequence. 
     At  220 , a precursor containing tantalum is pulsed. In an embodiment, a tantalum ethoxide, Ta(OC 2 H 5 ) 5 , may be used to deposit tantalum by atomic layer deposition. In an embodiment, a tantalum halide precursor, such as TaCl 5 , may be used to deposit tantalum by atomic layer deposition. The tantalum may be deposited before depositing hafnium in an atomic layer deposition process for forming a hafnium tantalum oxide. In addition, the pulsing of the tantalum precursor may use a pulsing period that provides uniform coverage of a monolayer on the surface or may use a pulsing period that provides partial formation of a monolayer on the surface during a tantalum sequence. 
     In an embodiment, a hafnium tantalum oxide may be formed substantially as a stoichiometric hafnium tantalum oxide. In an embodiment, a hafnium tantalum oxide may be formed substantially as a non-stoichiometric hafnium tantalum oxide or a combination of non-stoichiometric hafnium tantalum oxide and stoichiometric hafnium tantalum oxide. In an embodiment, a hafnium-rich hafnium tantalum oxide may be formed by atomic layer deposition. In an embodiment, a tantalum-rich hafnium tantalum oxide may be formed by atomic layer deposition. In an embodiment, an amorphous hafnium tantalum oxide may be formed by atomic layer deposition. Alternatively, the dielectric layer may be forming containing the atomic layer deposited hafnium tantalum oxide layer and one or more layers of other dielectric materials including, but not limited to, dielectric nitrides, dielectric metal silicates, dielectric metal oxides including Al 2 O 3 , HfO 2 , Ta 2 O 5 , and lanthanide oxides. These one or more other layers of insulating oxides may be provided in stoichiometric form, in non-stoichiometric form, or a combination of stoichiometric insulating oxides and non-stoichiometric insulating oxides. 
     In the various embodiments, the thickness of a Hf x Ta y O z  film is related to the number of ALD cycles performed for each metal species and the growth rate associated with the selected permutations of sequences in the cycles. As can be understood by those skilled in the art, particular effective growth rates for the engineered Hf x Ta y O z  film can be determined during normal initial testing of the ALD system for processing a hafnium tantalum oxide dielectric for a given application without undue experimentation. 
     Atomic layer deposition of the individual components of the hafnium tantalum oxide layer allows for individual control of each precursor pulsed into the reaction chamber. Thus, each precursor is pulsed into the reaction chamber for a predetermined period, where the predetermined period can be set separately for each precursor. Additionally, for various embodiments for ALD formation of a hafnium tantalum oxide layer, each precursor can be pulsed into the reaction under separate environmental conditions. The substrate can be maintained at a selected temperature and the reaction chamber maintained at a selected pressure independently for pulsing each precursor. Appropriate temperatures and pressures may be maintained, whether the precursor is a single precursor or a mixture of precursors. During atomic layer deposition, the pulsing of the precursor gases is separated by purging the reaction chamber with a purging gas following each pulsing of a precursor. In an embodiment, nitrogen gas is used as the purging gas following the pulsing of each precursor used in a cycle to form a film of hafnium tantalum oxide. Additionally, the reaction chamber can also be purged by evacuating the reaction chamber. 
     In various embodiments, the structure of the interface between the dielectric layer and the substrate on which it is disposed is controlled to limit the inclusion of silicon oxide, since a silicon oxide layer would reduce the effective dielectric constant of the dielectric layer. The material composition and its properties for an interface layer are typically dependent on process conditions and the condition of the substrate before forming the dielectric layer. Though the existence of an interface layer may effectively reduce the dielectric constant associated with the dielectric layer and its substrate interface layer, a silicon oxide interface layer or other composition interface layer, may improve the interface density, fixed charge density, and channel mobility of a device having this interface layer. 
       FIG. 3  illustrates a flow diagram of elements for an embodiment of a method to form a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. This embodiment can be implemented with the atomic layer deposition system  100  of  FIG. 1 . At  305 , a substrate  110  is prepared. The substrate used for forming a transistor is typically a silicon or silicon containing material. In other embodiments, germanium, gallium arsenide, silicon-on-sapphire substrates, silicon-on-insulator, or other suitable substrates may be used. This exemplary preparation process includes cleaning substrate  110  and forming layers and regions of the substrate, such as drains and sources of a metal oxide semiconductor (MOS) transistor, prior to forming a gate dielectric. Alternatively, these active regions may be formed after forming the dielectric layer, depending on the over-all fabrication process implemented. In an embodiment, the substrate is cleaned to provide an initial substrate depleted of its native oxide. In an embodiment, the initial substrate is cleaned also to provide a hydrogen-terminated surface. In an embodiment, a silicon substrate undergoes a final hydrofluoric (HF) rinse prior to ALD processing to provide the silicon substrate with a hydrogen-terminated surface without a native silicon oxide layer. 
     Cleaning immediately preceding atomic layer deposition aids in reducing an occurrence of silicon oxide as an interface between a silicon based substrate and a hafnium tantalum oxide dielectric formed using the atomic layer deposition process. The material composition and its properties of an interface layer are typically dependent on process conditions and the condition of the substrate before forming the dielectric layer. Though the existence of an interface layer may effectively reduce the dielectric constant associated with the dielectric layer and its substrate interface layer, a SiO 2  interface layer or other composition interface layer, may improve the interface density, fixed charge density, and channel mobility of a device having this interface layer. In an embodiment, cleaning of the substrate surface may be followed by a surface nitridation at elevated temperatures in a nitrogen ambient. The nitrogen ambient may be a NH 3  ambient. In an embodiment, the surface nitridation is conducted at about 700° C. for about 10 seconds. Such a nitridation may be conducted after defining an active area and after a pre-gate formation cleaning. 
     The sequencing of the formation of the regions of the transistor being processed may follow typical sequencing that is generally performed in the fabrication of a MOS transistor as is well known to those skilled in the art. Included in the processing prior to forming a gate dielectric is the masking of substrate regions to be protected during the gate dielectric formation, as is typically performed in MOS fabrication. In this embodiment, the unmasked region includes a body region of a transistor, however one skilled in the art will recognize that other semiconductor device structures may utilize this process. Additionally, the substrate  110  in its ready for processing form is conveyed into a position in reaction chamber  120  for ALD processing. 
     At  310 , a precursor containing hafnium, such as a Hf(NO 3 ) 4  precursor, is pulsed into reaction chamber  120 . The Hf(NO 3 ) 4  precursor is pulsed into reaction chamber  120  through the gas-distribution fixture  140  onto substrate  110 . The flow of the HftNO 3 ) 4  precursor is controlled by mass-flow controller  156  from gas source  151 , where the Hf(NO 3 ) 4  precursor is maintained. In an embodiment, the substrate temperature is maintained at temperature ranging from about 160° C. to about 350° C. In an embodiment, the substrate temperature is maintained at about 180° C. by heating element  130 . The HftNO 3 ) 4  precursor reacts with the surface of the substrate  110  in the desired region defined by the unmasked areas of the substrate  110  to deposit hafnium. In other embodiments, HfCl 4  is used as the precursor containing hafnium. 
     At  315 , a first purging gas is pulsed into the reaction chamber  120 . In an embodiment, nitrogen is used as a purging gas and a carrier gas. The nitrogen flow is controlled by mass-flow controller  166  from the purging gas source  161  into the gas conduit  170 . Using the pure nitrogen purge avoids overlap of the precursor pulses and possible gas phase reactions. In an embodiment, argon gas or other inert gas may be used as the purging gas. Following the purge, a first oxygen-containing precursor is pulsed into the reaction chamber  120 , at  320 . 
     For a hafnium sequence using a Hf(NO 3 ) 4  precursor or a HfCl 4  precursor, water vapor may be selected as the precursor acting as a reactant to deposit hafnium and oxygen on the substrate  110 . The H 2 O vapor is pulsed into the reaction chamber  120  through gas conduit  170  from gas source  152  by mass-flow controller  157 . The water vapor aggressively reacts at the surface of substrate  110 . 
     Following the pulsing of the first oxygen-containing precursor, a second purging gas is injected into the reaction chamber  120 , at  325 . Nitrogen gas may be used to purge the reaction chamber after pulsing each precursor gas in the hafnium/oxygen sequence. In an embodiment, argon gas or other inert gas may be used as the purging gas. Excess precursor gas and reaction by-products are removed from the system by the purge gas in conjunction with the exhausting of the reaction chamber  120  using vacuum pump  182  through mass-flow controller  187 , and exhausting of the gas conduit  170  by the vacuum pump  181  through mass-flow controller  186 . 
     At  330 , a precursor containing tantalum is pulsed into reaction chamber  120 . In an embodiment, a tantalum ethoxide precursor is used. The Ta(OC 2 H 5 ) 5  is pulsed to the surface of the substrate  110  through gas-distribution fixture  140  from gas source  153  by mass-flow controller  158 . The Ta(OC 2 H 5 ) 5  is introduced onto the hafnium and oxygen formed during the hafnium sequence. In an embodiment, during pulsing of the precursor containing tantalum, the substrate may be held between about 250° C. and about 350° C. by the heating element  130 . In an embodiment, a tantalum halide may be used as a precursor. 
     At  335 , a third purging gas is introduced into the system. In an embodiment, nitrogen may be used as a purging and carrier gas. Alternatively, purified argon may be used as a purging gas. The flow of the third purging gas is controlled by mass-flow controller  167  from the purging gas source  162  into the gas conduit  170  and subsequently into the reaction chamber  120 . 
     At  340 , a second oxygen-containing precursor is pulsed into the reaction chamber  120 . Water vapor may be used as the precursor acting as an oxidizing reactant to interact at the substrate  110 . The water vapor is pulsed into the reaction chamber  120  through gas conduit  170  from gas source  154  by mass-flow controller  159 . The water vapor aggressively reacts at the surface of substrate  110  to form a hafnium tantalum oxide. 
     At  345 , a fourth purging gas is injected into the reaction chamber  120 . In an embodiment, nitrogen gas is used as the fourth purging gas to purge the reaction chamber. Alternatively, argon gas may be used as the fourth purging gas. Excess precursor gas and reaction by-products are removed from the system by the purge gas in conjunction with the exhausting of the reaction chamber  120  using vacuum pump  182  through mass-flow controller  187 , and exhausting of the gas conduit  170  by the vacuum pump  181  through mass-flow controller  186 . 
     At  350 , it is determined whether the hafnium tantalum oxide film is of the desired thickness, t. The thickness of a hafnium tantalum oxide film after one cycle is determined by the pulsing periods used in the tantalum sequence and the hafnium sequence at a given temperature. Typically, at a given temperature, the pulsing periods can vary over a significant range above some minimum pulse time for the precursors, without substantially altering the growth rate. Once a set of periods for one cycle is determined, the growth rate for the hafnium tantalum oxide film will be set at a value such as N nm/cycle. For a desired hafnium tantalum oxide film thickness in an application such as forming a gate dielectric of a MOS transistor, the ALD process should be repeated for t/N cycles. The desired thickness should be completed after t/N cycles. If less than t/N cycles have been completed, the process starts over at  310  with the pulsing of the precursor containing tantalum. If t/N cycles have completed, no further ALD processing is required and the hafnium tantalum oxide film is completed. Once the total number of cycles to form the desired thickness has been completed, the dielectric film containing the hafnium tantalum oxide layer may optionally be annealed. In an embodiment, completion of a desired composition of the dielectric layer is followed by annealing in a nitrogen ambient. The annealing may be performed at about 950° C. for approximately 30 seconds. The Hf x Ta y O z  layer may be amorphous after annealing. 
     At  360 , after forming the hafnium tantalum oxide layer, processing the device having the dielectric layer containing the hafnium tantalum oxide layer is completed. In an embodiment, completing the device includes further processing of the dielectric layer to include layers of other dielectric materials. In an embodiment, completing the device includes completing the formation of a transistor. In another embodiment, completing the device includes completing the formation of a capacitor. Alternatively, completing the process includes completing the construction of a memory device having an array with access transistors formed with gate dielectrics containing an atomic layer deposited hafnium tantalum oxide layer. Further, in another embodiment, completing the process includes the formation of an electronic system including an information handling device that uses electronic devices with transistors formed with dielectric films containing an atomic layer deposited hafnium tantalum oxide layer. 
     Embodiments for methods similar to the embodiment of  FIG. 3  may include numerous permutations for forming the hafnium tantalum oxide layer. In an embodiment, the tantalum sequence is conducted before the hafnium sequence. A hafnium/tantalum cycle may include a number, x, of tantalum sequences and a number, y, of hafnium sequences. The number of sequences x, y may be selected to engineer the relative amounts of tantalum to hafnium. In an embodiment, the number of sequences x and y, along with associated pulsing periods and times, is selected to form a hafnium tantalum oxide with substantially equal amounts of tantalum and hafnium. In an embodiment, the number of sequences is selected with x=y. In an embodiment, the number of sequences x and y are selected to form a tantalum-rich hafnium tantalum oxide. Alternatively, the number of sequences x and y are selected to form a hafnium-rich hafnium tantalum oxide. In an embodiment, tantalum makes up about 43% of the hafnium tantalum oxide. The dielectric may be formed as HfO 2  doped with Ta 2 O 5 . In an embodiment, one or more sequences of depositing tantalum metal and one or more sequences of depositing hafnium metal are conducted before introducing a reactant precursor to oxidize the tantalum and hafnium. In an embodiment using metal depositing sequences, a mixture of tantalum and hafnium may be provided on the substrate surface that is oxidized when the reactant oxidizing precursor is introduced to the substrate surface. In an embodiment, an amorphous hafnium tantalum oxide layer is formed. 
     In an embodiment, the hafnium tantalum oxide layer may be doped with zirconium or a lanthanide. The doping may be employed to enhance the leakage current characteristics of the dielectric layer containing the hafnium tantalum oxide by providing a disruption or perturbation of the hafnium tantalum oxide structure. Such doping may be realized by substituting a sequence of a dopant for a tantalum sequence or a hafnium sequence. The choice for substitution may depend on the form of the hafnium tantalum oxide structure with respect to the ratio of tantalum atoms to hafnium desired in the oxide. To maintain a substantially hafnium tantalum oxide, the amount of dopant inserted into the oxide may be limited to a relatively small fraction of the total number of tantalum and hafnium atoms. Such a fraction may be 10 percent or less. In an embodiment, to maintain a substantially hafnium tantalum oxide, the amount of dopant in the oxide may be limited to a relatively small fraction of the tantalum or the hafnium atoms based on which material is selected to have the smallest number of atoms. Such a fraction may be 10 percent or less. 
     Various embodiments for fabricating a hafnium tantalum oxide may provide a hafnium tantalum oxide that is amorphous. However, crystallization of an atomic layer deposited hafnium tantalum oxide may occur above 1000° C. Embodiments for ALD formation of a hafnium tantalum oxide layer may fabricate an electrically stable device containing this oxide layer with limited mobility degradation, in a process that provides reduced complexity. 
     Embodiments providing a hafnium tantalum oxide layer between a gate and a body region over which the gate is formed allows for the use of thin dielectrics in electronic devices. Such a thin dielectric may be disposed between a floating gate and a control gate above a body region in an electronic device. Dielectrics containing a hafnium tantalum oxide layer may be provided with a thickness less than 50 Å. Embodiments may include dielectrics having a thickness less than 30 Å. Further, the embodiments described herein provide a process for growing a hafnium tantalum oxide layer having a wide range of useful equivalent oxide thickness, t eq , associated with a dielectric constant in the range from about 16 to about 26. This range of dielectric constants provides for a t eq  ranging from about 15% to about 25% relative to a given silicon dioxide thickness. In an embodiment, a dielectric layer containing a hafnium tantalum oxide layer has a t eq  ranging from about 4 Å to about 30 Å. In an embodiment, a dielectric layer containing a hafnium tantalum oxide layer has a t eq  of less than 5 Å. 
     Dielectric films employing a hafnium tantalum oxide layer as a replacement for a silicon oxide layer have useful characteristics in comparison with other metal oxides such as hafnium oxide. Hafnium tantalum oxide layers may be formed without an appreciable flat band voltage shift. MOS capacitors using a hafnium tantalum oxide dielectric may provide improved hysteresis characteristics as compared to HfO 2 . In addition, a Hf x Ta y O z  layer may provide a reduction in interface states density (D it ) compared to HfO 2 , where the tantalum aids in suppressing interface traps associated with HfO 2 . For example, a Hf x Ta y O z  layer having a Ta concentration of about 43% may yield a D it  that may be a factor of ten lower than that of hafnium oxide. Another useful characteristic associated with employing hafnium tantalum oxide as compared to hafnium oxide is a higher electron mobility in n-channel MOSFETs (NMOSFETs) using the hafnium tantalum oxide. Hafnium tantalum oxide layers used in a transistor provide higher drain current and smaller sub-threshold swing as compared to a transistor using a hafnium oxide layer. Under a 1000 second stress, a shift in threshold voltage may be about 6.2 mV, which is about a factor of twenty lower than that of pure hafnium dioxide. A transistor structure using a hafnium tantalum oxide layer may be operated without an appreciable sub-threshold voltage swing or variations in transconductance compared to such a structure using a hafnium oxide layer under similar voltage stress. Additionally, a hafnium tantalum oxide may provide improved lifetime characteristics over a hafnium oxide. The relative improvement over a hafnium oxide may depend on tantalum concentration. For example, a 10-year lifetime operating voltage of a hafnium tantalum oxide using about 43% tantalum projects to about 2.58 V, while the operating voltage of a hafnium tantalum oxide using about 29% tantalum projects to about 2.47 V, both of which are higher operating voltages than a projected voltage of 1.3V for HfO 2 . 
     It can appreciated by those skilled in the art that the elements of a method for forming an atomic layer deposited hafnium tantalum oxide film in the embodiment of  FIG. 3  can be performed with various numbers of tantalum sequences relative to the number of hafnium sequences. In selecting the number of tantalum sequences and hafnium sequences relative to each other, a hafnium tantalum oxide film can be engineered with bandgap and dielectric constant characteristics ranging from that of HfO 2  to that of Ta 2 O 5  for a thin dielectric layer. In various embodiments, a dielectric layer of hafnium tantalum oxide is provided with a controlled interface between the dielectric layer and a substrate surface on which it is disposed. The selection of the ratio of tantalum to hafnium in the hafnium tantalum layer may be conducted in a trade-off process with improving the current leakage characteristics of the film. Additionally, the novel process can be implemented to form transistors, capacitors, memory devices, and other electronic systems including information handling devices. 
     A transistor  400  as depicted in  FIG. 4  may be constructed by forming a source region  420  and a drain region  430  in a silicon based substrate  410  where source and drain regions  420 ,  430  are separated by a body region  432 . Body region  432  defines a channel having a channel length  434 . A dielectric layer is disposed on substrate  410 . A gate  450  is formed over and contacts gate dielectric  440 . The dielectric is formed on substrate  410 . The resulting dielectric layer forms gate dielectric  440 . Gate dielectric  440  may be realized as a dielectric layer formed substantially of a hafnium tantalum oxide film. Gate dielectric  440  may be a dielectric layer containing one or more layers of dielectric material in which at least one layer is hafnium tantalum oxide film. 
     An interfacial layer  433  may form between body region  432  and gate dielectric  440 . In an embodiment, interfacial layer  433  may be limited to a relatively small thickness compared to gate dielectric  440 , or to a thickness significantly less than gate dielectric  440  as to be effectively eliminated. Forming the substrate, gate, and the source and drain regions may be performed using standard processes known to those skilled in the art. Additionally, the sequencing of the various elements of the process for forming a transistor may be conducted with standard fabrication processes, also as known to those skilled in the art. In an embodiment, gate dielectric  440  may be realized as a gate insulator in a silicon CMOS transistor. Use of such a gate dielectric including an atomic layer deposited hafnium tantalum oxide layer is not limited to silicon based substrates, but may be used with a variety of semiconductor substrates. 
       FIG. 5  shows an embodiment of a configuration of a floating gate transistor  500  having a hafnium tantalum oxide layer. Transistor  500  includes a silicon based substrate  510  with a source  520  and a drain  530  separated by a body region  532 . Body region  532  between source  520  and drain  530  defines a channel region having a channel length  534 . Located above body region  532  is a stack  555  including a gate dielectric  540 , a floating gate  552 , a floating gate dielectric  542 , and a control gate  550 . In an embodiment, floating gate  552  is formed over and contacts gate dielectric  540 . An interfacial layer  533  may form between body region  532  and gate dielectric  540 . In an embodiment, interfacial layer  533  may be limited to a relatively small thickness compared to gate dielectric  540 , or to a thickness significantly less than gate dielectric  540  as to be effectively eliminated. 
     Gate dielectric  540  includes a dielectric containing an atomic layer deposited hafnium tantalum oxide layer formed in embodiments similar to those described herein. Gate dielectric  540  may be realized as a dielectric layer formed substantially of hafnium tantalum oxide. Gate dielectric  540  may include multiple layers in which at least one layer is substantially hafnium tantalum oxide. In an embodiment, gate dielectric  540  may include multiple layers where a substantially hafnium tantalum oxide contacts body region  532 . 
     In an embodiment, floating gate dielectric  542  includes a dielectric layer having an atomic layer deposited hafnium tantalum oxide layer formed in embodiments similar to those described herein. Floating gate dielectric  542  may be realized as a dielectric layer formed substantially of hafnium tantalum oxide. Floating gate dielectric  542  may include multiple layers in which at least one layer is substantially hafnium tantalum oxide. In an embodiment, control gate  550  is formed over and contacts floating gate dielectric  542 . 
     Alternately, both gate dielectric  540  and floating gate dielectric  542  may be formed as dielectric layers including an atomic layer deposited hafnium tantalum oxide layer. Gate dielectric  540  and floating gate dielectric  542  may be realized by embodiments similar to those described herein with the remaining elements of the transistor  500  formed using processes known to those skilled in the art. 
     In an embodiment, gate dielectric  540  forms a tunnel gate insulator and floating gate dielectric  542  forms an inter-gate insulator in flash memory devices, where gate dielectric  540  and/or floating gate dielectric  542  include a hafnium tantalum oxide layer formed by atomic layer deposition. Use of dielectric layers configured in various embodiments is not limited to silicon based substrates, but may be used with a variety of semiconductor substrates. 
     The embodiments of methods for forming dielectric layers containing a hafnium tantalum oxide layer by atomic layer deposition may also be applied to forming capacitors in various integrated circuits, memory devices, and electronic systems. Such capacitors may be formed in addition to forming a transistor having a gate dielectric and/or an inter-gate dielectric containing an atomic layer deposited hafnium tantalum oxide layer. In an embodiment for forming a capacitor  600  illustrated in  FIG. 6 , a method includes forming a first conductive layer  610 , forming a dielectric layer  620  containing a hafnium tantalum oxide layer formed by atomic layer deposition on first conductive layer  610 , and forming a second conductive layer  630  on dielectric layer  620 . Dielectric layer  620  including a hafnium tantalum oxide layer may be formed using any of the embodiments described herein. 
     An interfacial layer  615  may form between first conductive layer  610  and dielectric layer  620 . In an embodiment, interfacial layer  615  may be limited to a relatively small thickness compared to dielectric layer  620 , or to a thickness significantly less than dielectric layer  620  as to be effectively eliminated. 
     Dielectric layer  620  may be realized as a dielectric layer formed substantially of hafnium tantalum oxide. Dielectric layer  620  may include multiple layers in which at least one layer is substantially hafnium tantalum oxide. In an embodiment, dielectric layer  620  may include multiple layers where a substantially hafnium tantalum oxide film contacts first conductive layer  610 . Embodiments for dielectric layer  620  in a capacitor include, but are not limited to, dielectrics in DRAM capacitors and dielectrics in capacitors in analog, radio frequency (RF), and mixed signal integrated circuits. 
     Various embodiments for a dielectric film containing a hafnium tantalum oxide layer formed by atomic layer deposition may provide for enhanced device performance by providing devices with reduced leakage current. In an embodiment, such improvements in leakage current characteristics may be attained by forming one or more layers of an atomic layer deposited hafnium tantalum oxide in a nanolaminate structure with other dielectric layers including other metal oxides such as tantalum oxide and/or hafnium oxide. The transition from one layer of the nanolaminate to another layer of the nanolaminate provides further disruption to a tendency for an ordered structure in the nanolaminate stack. The term “nanolaminate” means a composite film of ultra thin layers of two or more materials in a layered stack, where the layers may be alternating layers of materials of the composite film. Typically, each layer in a nanolaminate has a thickness of an order of magnitude in the nanometer range. Further, each individual material layer of the nanolaminate may have a thickness as low as a monolayer of the material or as high as 20 nanometers. In an embodiment, a TaO x /Hf x Ta y O z  nanolaminate contains layers of a tantalum oxide and a hafnium tantalum oxide. In an embodiment, a HfO x /Hf x Ta y O z  nanolaminate contains layers of a hafnium oxide and a hafnium tantalum oxide. A TaO x /Hf x Ta y O z /HfO x  nanolaminate contains layers of tantalum oxide, hafnium oxide, and hafnium tantalum oxide. 
       FIG. 7  depicts a nanolaminate structure  700  for an embodiment of a dielectric structure including an atomic layer deposited hafnium tantalum oxide layer. In an embodiment, nanolaminate structure  700  includes a plurality of layers  705 - 1 ,  705 - 2  to  705 -N, where at least one layer contains a hafnium tantalum oxide film formed according to an embodiment herein. The other layers may be other dielectric layers or dielectric metal oxides. The sequencing of the layers depends on the application. In an embodiment, an atomic layer deposited hafnium tantalum oxide film is the first layer formed on a substrate. In an embodiment, nanolaminate structure  700  contains an atomic layer deposited hafnium tantalum oxide film in contact with conductive contact  710  and/or conductive contact  720 . The effective dielectric constant associated with nanolaminate structure  700  is that attributable to N capacitors in series, where each capacitor has a thickness defined by the thickness of the corresponding layer. By selecting each thickness and the composition of each layer, a nanolaminate structure can be engineered to have a predetermined dielectric constant. Embodiments for structures such as nanolaminate structure  700  may be used as nanolaminate dielectrics in NROM flash memory devices as well as other integrated circuits. 
     Transistors, capacitors, and other devices having dielectric films containing a hafnium tantalum oxide layer formed by atomic layer deposition by various embodiments similar to the methods described herein may be implemented into memory devices and electronic systems including information handling devices. Embodiments of these information handling devices may include wireless systems, telecommunication systems, and computers. Further, embodiments of electronic devices having dielectric films containing an atomic layer deposited hafnium tantalum oxide film may be realized as integrated circuits. 
       FIG. 8  illustrates a diagram for an electronic system  800  having one or more devices having a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer fabricated according to various embodiments. Electronic system  800  includes a controller  805 , a bus  815 , and an electronic device  825 , where bus  815  provides electrical conductivity between controller  805  and electronic device  825 . In various embodiments, controller  805  and/or electronic device  825  include an embodiment for a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer. Electronic system  800  may include, but is not limited to, information handling devices, wireless systems, telecommunication systems, fiber optic systems, electro-optic systems, and computers. 
       FIG. 9  depicts a diagram of an embodiment of a system  900  having a controller  905  and a memory  925 . Controller  905  and/or memory  925  may include a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer according to various embodiments. System  900  also includes an electronic device  935  and a bus  915 , where bus  915  provides electrical conductivity between controller  905  and electronic device  935 , and between controller  905  and memory  925 . Bus  915  may include an address, a data bus, and a control bus, each independently configured. Alternately, bus  915  may use common conductive lines for providing address, data, and/or control, the use of which is regulated by controller  905 . In an embodiment, electronic device  935  may be additional memory configured in a similar manner as memory  925 . An embodiment may include an additional peripheral device or devices  945  coupled to bus  915 . In an embodiment, controller  905  is a processor. Any of controller  905 , memory  925 , bus  915 , electronic device  935 , and peripheral devices  945  may include a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer formed according to various embodiments. System  900  may include, but is not limited to, information handling devices, telecommunication systems, and computers. 
     Peripheral devices  945  may include displays, additional storage memory, or other control devices that may operate in conjunction with controller  905 . Alternately, peripheral devices  945  may include displays, additional storage memory, or other control devices that may operate in conjunction with controller  905  and/or memory  925 . 
     Memory  925  may be realized as a memory device containing a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer formed according to various embodiments. It will be understood that embodiments are equally applicable to any size and type of memory circuit and are not intended to be limited to a particular type of memory device. Memory types include a DRAM, SRAM (Static Random Access Memory) or Flash memories. Additionally, the DRAM could be a synchronous DRAM commonly referred to as SGRAM (Synchronous Graphics Random Access Memory), SDRAM (Synchronous Dynamic Random Access Memory), SDRAM II, and DDR SDRAM (Double Data Rate SDRAM), as well as Synchlink or Rambus DRAMs and other emerging DRAM technologies. 
     Formation of a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer may be amorphous and possess smooth surfaces. Such hafnium tantalum oxide films may provide enhanced electrical properties due to their smoother surface resulting in reduced leakage current. Additionally, such dielectric layers provide a significantly thicker physical thickness than a silicon oxide layer having the same equivalent oxide thickness, where the increased thickness would also reduce leakage current. These properties of embodiments of dielectric layers allow for application as dielectric layers in numerous electronic devices and systems. 
     Capacitors, transistors, higher level ICs or devices including memory devices, and electronic systems are constructed utilizing the novel process for forming a dielectric film having an ultra thin equivalent oxide thickness, t eq . Gate dielectric layers or films including a dielectric layer containing an atomic layer deposited hafnium tantalum oxide layer are formed having a dielectric constant (κ) substantially higher than that of silicon oxide. These dielectric films are capable of a t eq  thinner than SiO 2  gate dielectrics of the same physical thickness. Alternately, the high dielectric constant relative to silicon dioxide allows the use of much larger physical thickness of these high-K dielectric materials for the same t eq  of SiO 2 . Forming the relatively larger thickness aids in processing gate dielectrics and other dielectric layers in electronic devices and systems. 
     Although specific embodiments have been illustrated and described herein, it will be appreciated by those of ordinary skill in the art that any arrangement that is calculated to achieve the same purpose may be substituted for the specific embodiments shown. This application is intended to cover any adaptations or variations of embodiments of the present invention. It is to be understood that the above description is intended to be illustrative, and not restrictive, and that the phraseology or terminology employed herein is for the purpose of description and not of limitation. Combinations of the above embodiments and other embodiments will be apparent to those of skill in the art upon studying the above description. The scope of the present invention includes any other applications in which embodiments of the above structures and fabrication methods are used. The scope of the embodiments of the present invention should be determined with reference to the appended claims, along with the full scope of equivalents to which such claims are entitled.