Abstract:
An atomic layer deposition method of forming a solid thin film layer containing silicon. A substrate is loaded into a chamber. A first portion of a first reactant is chemisorbed onto the substrate, and a second portion of the first reactant is physisorbed onto the substrate. The physisorbed portion is purged from the substrate and the chamber. A second reactant is injected into the chamber. A first portion is chemically reacted with the chemisorbed first reactant to form a silicon-containing solid on the substrate. The first reactant is preferably Si[N(CH 3 ) 2 ] 4 , SiH[N(CH 3 ) 2 ] 3 , SiH 2 [N(CH 3 ) 2 ] 2  or SiH 3 [N(CH 3 ) 2 ]. The second reactant is preferably activated NH 3 .

Description:
The present invention relates to a method of forming Si 3 N 4  and SiO 2  thin film by utilizing atomic layer deposition method and employing trisdimethylaminosilane {HSi[N(CH 3 ) 2 ] 3 }, (hereinafter, referred to as “TDMAS”) as a reactant. 
     BACKGROUND OF THE INVENTION 
     Generally, Si 3 N 4  and SiO 2  thin films are formed in semiconductor devices by utilizing deposition methods such as Chemical Vapor Deposition (CVD), Low Pressure Chemical Vapor Deposition (LPCVD), plasma-enhanced chemical vapor deposition (PECVD). 
     CVD-based methods often have drawbacks that limit their usefulness in the manufacture of semiconductor devices that would benefit by inclusion of thin films of Si 3 N 4 . In a typical CVD method, a thin film of Si 3 N 4  is deposited at a relatively high temperature, which in general is less preferable than a lower temperature process due to the possibility of adverse thermal effects on the device. A Si 3 N 4  layer deposited by CVD is also subject to geometric hindrances causing thickness variations across the surface of the device. The thickness of the thin film formed around densely packed features on the surface can be less than the thickness of the film around less densely packed features. This problem is known as a pattern loading effect. 
     LPCVD suffers from shortcomings as well. The hydrogen content of the LPCVD-manufactured thin film is usually high, and step coverage of the surface is not good. Since the film growth rate is relatively slow when using LPCVD, the processing time required to grow a film of suitable thickness is relatively long. The long processing time exposes the substrate to a relatively high temperature for a long time, and results in a high thermal budget associated with the LPCVD process. 
     Atomic layer deposition (ALD) has been proposed as an alternative to CVD-based depositions methods for the formation of Si 3 N 4  and SiO 2  thin films. ALD is a surface controlled process conducted in a surface kinetic regime, and which results in two-dimensional layer-by-layer deposition on the surface. Goto et al. describe an ALD deposition method using dichlorosilane (DCS) and NH3 plasma to form a Si 3 N 4  film. (Appl. Surf. Sci., 112, 75-81 (1997); Appl. Phys. Lett. 68(23), 3257-9(1996)). However, the properties of the thin film manufactured by the method described in Goto are not suitable. The Cl content (0.5%), and O content are unacceptably high. These, combined with a measured Si:N ratio of 41:37 indicate that this method does not form a near-stoichiometric film of Si 3 N 4 . In addition, the growth rate of 0.91 angstroms per cycle of 300 seconds is not as high as would be necessary for commercial applications. 
     Klaus et al. describe an ALD method of forming a Si 3 N 4  film by reacting SiCl 4  and NH 3 . See, U.S. Pat. No. 6,090,442, and Surf. Sci., 418, L14-L19 (1998). The characteristics of the thin film manufactured by this method are better than that achieved by Goto et al. The ratio of Si:N=1:1.39, and the Cl, H and O contents are acceptably low. However, the cycle time of 10 minutes to grow a 2.45-angstrom film is too long, making any commercial application impractical. 
     It has also been proposed to use Si 2 Cl 6  (HCD) and N2H4 to deposit a thin Si 3 N 4  film by ALD. (Appl. Surf. Sci., 112, 198-203 (1997)). While the stoichiometry, Cl and H content of such films are suitable, they exhibit an unacceptably high oxygen content, rendering such films unsuitable for the uses described above. 
     ALD has also been proposed as a method of depositing SiO 2  thin films. For example, it has been proposed to depositing process using SiCl 4  and H 2 O. Appl. Phys. Lett. 70(9), 1092 (1997). However, the cycle time in the proposed process is too long for commercial application. U.S. Pat. No. 6,090,442 discloses a catalyzed process wherein a SiO 2  film is deposited using SiCl 4  and H 2 O, with C 5 H 5 N or NH 3  as a catalyst. The quality of the SiO 2  film obtained with this process is not good because of the low deposition temperatures. A process utilizing Si(NCO) 4  &amp; TEA has been proposed (Appl. Surf. Sci. Vol. 130-132, pp. 202-207 (1998)), but also suffers from low quality due to low processing temperatures. The same is true of a proposed process using Si(NCO) x , and H 2 O, (J. Non-crystalline Solids, Vol. 187, 66-69(1995)). 
     Therefore, despite a long-recognized potential for widespread application, a need remains for a novel method of forming Si 3 N 4  and SiO 2  thin films that meet the following criteria: low thermal budget process; excellent step coverage; no pattern loading effect; Si:N ratio consistent with Si 3 N 4 ; excellent thickness control and uniformity; minimal number of particulate inclusions; low impurity content; and a film growth rate that makes commercial application practical. 
     In order to accomplish the above-described items, an atomic layer deposition (ALD) employing TDMAS as a reactant is utilized for the preparation of Si3N4 and SiO2 thin films in the present invention. 
     SUMMARY OF THE INVENTION 
     The present invention is embodied in an atomic layer deposition method of forming a solid thin film layer containing silicon in which a substrate is loaded into a chamber. A first reactant containing Si and an aminosilane is injected into the chamber, where a first portion of the first reactant is chemisorbed onto the substrate, and a second portion of the first reactant is physisorbed onto the substrate. The physisorbed second portion of the first reactant is then removed from the substrate, by purging and flushing the chamber in one preferred embodiment. A second reactant is then injected into the chamber, where a first portion of the second reactant is chemically reacted with the chemisorbed first portion of the first reactant to form a silicon-containing solid on the substrate. The non-chemically reacted portion of the second reactant is then removed from the chamber. In one preferred embodiment, the silicon-containing solid formed on the substrate is a thin film layer, a silicon nitride layer for example. In other preferred embodiments, the first reactant is at least one selected from the group consisting of Si[N(CH 3 ) 2 ] 4 , SiH[N(CH 3 ) 2 ] 3 , SiH 2 [N(CH 3 ) 2 ] 2  and SiH 3 [N(CH 3 ) 2 ]. The second reactant is preferably activated NH 3 . The chamber pressure is preferably maintained in a range of 0.01-100 torr. and in preferred embodiments can be maintained constant throughout the process, or can be varied in at least one of the four steps. One or more of the foregoing steps can be repeated to achieve a thicker solid on the substrate. 
     In various embodiments, silicon-containing solids formed by the methods of the invention have a dry etch selectivity with respect to Si of a semiconductor device when formed as an active mask nitride, with respect to WSix and doped poly-Si of a semiconductor device when formed as a gate mask nitride, and with respect to W and Ti/TiN of a semiconductor device when formed as a bit line mask nitride. The silicon-containing solid formed on the substrate can also be formed to act as a CMP stopper, or as an insulating layer having a dry etch selectivity with respect to SiO 2  of a semiconductor device (spacer). In other embodiments, the silicon-containing solid formed on the substrate is an insulating layer having an HF wet etch selectivity with respect to SiO 2  of a semiconductor device to act as a wet stopper. 
     The silicon-containing solid formed on the substrate can serve as a gate dielectric of a semiconductor device, a layer formed between a Ta 2 O 5  layer and a capacitor storage node of a semiconductor device, as a dielectric layer of a capacitor of a semiconductor device, or as an STI liner of a semiconductor device. 
     In other embodiments, the silicon-containing solid formed on the substrate is silicon oxide, and in one or more of those embodiments the second reactant is selected from the group consisting of H2O, H2O2, O2 plasma and O3 plasma. 
     In yet another embodiment, at least one of the first and second silicon-containing solids is a metal silicate wherein the metal is selected from the group consisting of Al, Hf, Zr, Ti, and Ta. 
     These and other features of the invention will now be described with reference to the drawings. 
    
    
     BRIEF DESCRIPTION OF THE DRAWINGS 
     The above objective and advantages of the present invention will become more apparent by describing in detail preferred embodiments thereof with reference to the attached drawings in which: 
     FIGS. 1,  2 ,  3 ,  4 , and  5  describe the steps of processes for forming a thin film of Si3N4 using an atomic layer deposition according to a preferred embodiment of the present invention. 
     FIG. 6 is a schematic diagram of a thin film manufacturing apparatus used for a thin film manufacturing method according to the present invention. 
     FIG. 7 is a flowchart describing the thin film manufacturing methods according to the present invention. 
     FIG. 8 is a graph showing the thickness of a Si 3 N 4  film formed per cycle using a manufacturing method according to one preferred embodiment of the present invention. 
     FIG. 9 is a graph showing the variation in Si 3 N 4  film thickness and uniformity of a film as the TDMAS dosing time is varied in a method according to a preferred embodiment of the present invention. 
     FIG. 10 is a graph showing the variation in Si 3 N 4  film thickness and uniformity of a film as the NH 3  plasma generator power is varied in a method according to a preferred embodiment of the present invention. 
    
    
     DETAILED DESCRIPTION OF THE INVENTION 
     The following description of preferred embodiments will begin with an explanation of the process steps of the methods, followed by descriptions of specific examples of preferred embodiments of the invention. 
     Referring now to FIGS. 1-6, a substrate  1  such as silicon ( 100 ) is placed in a chamber  3  (see FIG.  6 ), which is then evacuated to a pressure of about 2 Torr. Substrate  1  is heated to about 550° C. A stream  2  of 500 sccm of TDMAS in an Ar carrier gas is then introduced into the chamber for 15 seconds. The flow of stream  2  is then stopped, and the chamber is left undisturbed for between 15 and 165 seconds. 
     During this time, a first portion of the TDMAS chemisorbs and forms a layer  4  on the surface of substrate  1 . A second portion of the TDMAS molecules physically attaches (physisorbs) onto, and is loosely held to the chemisorbed layer of TDMAS. The chamber  3  is then purged with N 2  for 5 seconds, and vacuum purged for 5 seconds. During these purging steps, the non-chemically absorbed portions of TDMAS are removed from the chamber, leaving the chemisorbed layer  4  of TDMAS intact on the substrate  1  (FIG.  2 ). Referring now to FIG. 3, a stream  6  of 2000 sccm of Ar containing activated NH 3  is then introduced into chamber  3  for 30 seconds, while maintaining a reduced chamber pressure of 0.5 Torr and a substrate temperature of 550° C. A portion of the activated NH 3  reacts with the chemisorbed TDMAS on the substrate to form a layer  8  of Si 3 N 4  (FIG.  4 ). In one embodiment, the activated NH 3  is a plasma is generated in a plasma generator that is operated at about 400 watts, but the power can be varied and the invention is not intended to be limited to a particular plasma chamber power level. After the NH 3 -containing stream has flowed into the chamber for 30 seconds, chamber  3  is then purged with N 2  for 5 seconds, and then vacuum purged for 5 seconds. The steps of introducing TDMAS into chamber  3 , purging, introducing NH 3  into the chamber, and purging again can be repeated to achieve any desired thickness of Si 3 N 4  layer  8 . The formation of the Si 3 N 4  layer  8  is now complete. 
     FIG. 6 is a schematic diagram of a thin film manufacturing apparatus used for the thin film manufacturing method according to the present invention. FIG. 7 is a flowchart describing the thin film manufacturing method according to the present invention. The embodiment described above will now be described with reference to FIGS. 6-10. After loading a substrate  1 , for example a ( 100 ) silicon substrate, into a chamber  3 , the chamber is brought to a pressure of about 2 Torr, and to a temperature of about 550° C. using a heater  5  (step  100 ). The first reactant stream containing TDMAS is injected into chamber  3  for 30 seconds while the substrate is maintained at 550° C. and about 2 Torr. (step  105 ). The TDMAS is vaporized to form a first reactant stream  6  by injecting 500 sccm of Ar carrier gas from a source  19  into the first bubbler  12 , which contains liquid TDMAS at a temperature of about 25° C. The combined TDMAS and Ar gas stream is then injected into chamber  3  through a first gas line  13  and a shower head  15  for a period of about 30 seconds, as described above. Chamber  3  is then purged with pure Ar for 5 seconds, and then vacuum purged by pump  7  for 5 seconds. The invention is not intended to be limited to this particular purging scheme, and is intended to include alternate purging sequences that result in the removal of the physisorbed TDMAS from the chemisorbed surface layer of TDMAS. 
     The second reactant gas stream of activated NH3 in an Ar carrier is then injected into chamber  3  through gas line  16  and showerhead  15  for about 30 seconds at a rate of about 2000 sccm. During this step the substrate  1  is maintained at 550° C. and the chamber pressure is maintained at about 0.5 Torr (step  115  in FIG.  7 ). In one embodiment, the NH 3  in the second reactant gas stream is vaporized by bubbling Ar from gas source  19  through liquid NH 3    14  held at about 25° C. in a second bubbler  17 . The NH3 and Ar stream is then passed through a remote plasma generator (not shown), and then introduced into chamber  3  through gas line  16  and showerhead  15  for about 30 seconds at a rate of about 2000 sccm. 
     As represented in FIGS. 3 and 4, a portion of the NH3 in the second reactant stream reacts with the TDMAS chemisorbed on the substrate  1  to form a layer of Si 3 N 4 . As the layer of Si 3 N 4  is formed on the substrate, a second portion of the NH3 in the second reactant stream is physisorbed onto the Si 3 N 4  layer. The chamber  3  is then purged using an Ar stream for 5 seconds, followed by vacuum purging using pump  7  (step  120 ). However, the physisorbed second reactant can be also removed by vacuum pumping the chamber without first purging with an inert gas. 
     After purging the unreacted NH 3  from chamber  3 , the Si 3 N 4  film thickness is measured (step  125 ). If additional layer thickness is required, steps  105  through  125  are repeated until the desired film thickness is achieved. When the desired thickness has been reached, the manufacturing process is completed by returning the temperature and the pressure of the chamber to normal. (step  130 ). 
     As shown in FIG. 8, in the foregoing method for the formation of an Si 3 N 4  layer, the deposition rate is 1.35 Å/cycle, and the film thickness demonstrates a linear relationship with respect to the number of cycles. The refractive index of the deposited material was measured at 2.0 at the wavelength of 632.8 nm, confirming that the deposited layer is stoichiometric Si3N4. The tensile stress of the film was measured at 5E10 dyne/cm2. The hydrogen content and the carbon content were both very low at about 1 at % or less, and no oxygen was detected. A step coverage of 95% or over was accomplished over a contact-type structure having an aspect ratio of 8:1. A wet etch rate with a 200:1 aqueous HF solution was relatively low at about 10 Å/min, providing the desired wet etch selectivity that is a useful feature of Si 3 N 4  thin films. 
     Referring to FIG. 9, when considering the change of growth rate with respect to the amount of TDMAS exposure, which is a typical ALD deposition characteristic, it was confirmed that no change of the growth rate was detected from a total 60 second exposure time (flow for 15 seconds &amp; hold for 45 seconds) under the above-described conditions. This would seem to indicate that an exposure time of 60 seconds results in a saturation of the substrate surface. In addition, when the TDMAS flowed for 30 seconds, the same growth rate was obtained as when the flowing time was 15 seconds and the holding time was 45 seconds or more. 
     Referring now to FIG. 10, the effect of the RF power level in the plasma generator was determined. Recall that in the method described above, after the substrate was exposed to TDMAS and the chamber purged, activated NH 3  was introduced into the chamber. As shown in FIG. 10, the use of activated NH 3  is an important aspect of the claimed methods. When the RF power in the power generator was 0, and therefore there was no activated NH3 introduced into the chamber, there was no Si 3 N 4  film deposition at all, indicating no reaction between non-activated NH 3  and the TDMAS on the substrate. Between 0 and 0.4 kW, the deposition rate of the film increased in a linear relationship as shown. From 0.4 kW up, the growth rate increased little if at all, demonstrating a deposition rate relationship that is typical of ALD. 
     In other embodiments, the ALD process described above can be implemented by using TDMAS with H 2 O, H 2 O 2 , activated O 2  (for example, O 3 , O 2  remote plasma, etc.). In still other embodiment, the ALD process described above can be utilized for the formation of a silicate, which is a dielectric substance having a larger dielectric constant than that of SiO 2 . In those embodiments, the process can be implemented by use of a metal oxide and TDMAS for forming a silicate layer. 
     The foregoing preferred embodiments are intended to be illustrative rather than limiting. Those of skill in the art will recognize that changes and modifications to the invention as described above are possible without departing from the scope of the following claims.