Abstract:
An embedded electroconductive layer is disclosed which comprises an opening part or a depressed part  3  formed in an insulating film  2  on a substrate  1 , a barrier layer for covering the opening part or the depressed part, a metal growth promoting layer  5  on the barrier layer, and an electroconductive layer  6  embedded in the opening part or the depressed part via the barrier layer  4  and the metal growth promoting layer  5.

Description:
This is divisional, of application Ser. No. 08/959,763, filed Oct. 29, 1997 U.S. Pat. No. 6,090,702 which in turn is a divisional of Ser. No. 08/660,524 (U.S. Pat. No. 5,736,192) filed Jun. 7, 1996. 
    
    
     BACKGROUND OF THE INVENTION 
     1. Field of the Invention 
     This invention relates to an embedded electroconductive layer and a method for the formation thereof. It relates more particularly to an embedded interconnection layer using Cu and Al or a connecting layer (plug) for joining an upper and a lower interconnection layer and a method for the formation thereof. 
     2. Description of the Prior Art 
     For the purpose of lowering the resistance offered by an interconnection layer, the feasibility of substituting a Cu interconnection layer for the conventional Al interconnection layer has been the subject of a diligent study. Cu has lower resistivity than Al and about twice as high electromigration resistance as Al. 
     Generally, the formation of a layer of fine wiring lines requires resorting to dry etching. 
     Cu, however, encounters the problem that the conventional RIE (reactive ion etching) technique fails to afford an ample etching rate at low temperatures because a halogenide of Cu has a low vapor pressure. It also has the problem of rendering anisotropic etching difficult. 
     The feasibility of a method which is called damascene and uses the self-aligning technique for the purpose of solving such problems as mentioned above is now being studied. 
     The damascene method resides in forming an embedded interconnection layer as follows. First a Cu layer is deposited in grooves and contact holes formed in an insulating layer in conformity with a wiring pattern. Then, the unwanted parts of the Cu layer that protrude from the grooves and the contact holes are removed by chemical mechanical polishing (CMP). 
     Among the methods available at all for the deposition of Cu in this case is counted the CVD method that excels in step coverage. The combination of the sputtering method deficient in step coverage with the reflow method is also available. Of these two methods, the former CVD (chemical vapor deposition) method is expected to grow into a prospective technique for the formation of a Cu interconnection layer fit for future trend toward increasing fineness of circuitry. 
     Further, Cu easily diffuses in SiO 2 , forms a deep sublevel in a silicon semiconductor, and curtails the service life of minority carriers. In the formation of a Cu interconnection layer by the damascene method, a barrier metal layer such as the TiN layer is formed on an SiO 2  layer and a Cu layer is grown thereon for the purpose of preventing Cu from diffusing in the SiO 2  (“Advanced Metallization for ULSI Application,” compiled by V. S. Rana et al., written by J. A. T. Norman, D. A. Roberts, A. K. Hochberg, and R. Laxman, and published by MRS, Pittsburgh, 1993). 
     When a Cu layer is grown by the CVD method on such a CVD-TiN layer as mentioned above, an anneal performed in the neighborhood of 600° C. tends to induce an alloying reaction between Cu and the barrier metal, though the incubation time between the time the step of deposition starts and the time the actual deposition of film begins decreases in proportion as the degree of oxidation on the surface of the barrier layer decreases. The growth of the Cu layer under discussion, therefore, encounters the problem that the CVD-TiN layer does not function as a barrier metal. 
     When a TiN layer which has a higher oxygen concentration than the CVD-TiN layer and is formed by the sputtering technique (hereinafter referred to as “PVD (physical vapor deposition)-TiN layer”) is used for the purpose of exalting the barrier property, the problem ensues that the incubation time is elongated. 
     The cause for the elongation of the incubation time is as follows. It has been reported (S. Cohen et al., Appl. Phys. Lett., Vol. 60(1), 6 January 1992 p.50-52) that during the deposition of a Cu layer using hexafluoroacetylacetonate trimethylvinyl silane Cu:Cu (hfac) TMVS as a precursor, for example, the precursor is caused to undergo decomposition and precipitate Cu owing to the donation of electrons from the surface of the ground layer. When the barrier layer constituting a ground layer has a high oxygen concentration and exhibits low metallicity, therefore, the incubation time is suffered to elongate because the donation of electrons from the surface of the barrier layer does not easily occur. 
     When an embedded electroconductive layer is formed by having an insulating film such as of copper embedded through the medium of a barrier layer in a groove as described above, this barrier layer is demanded to fulfill such mutually contradicting requirements as enhancing the barrier property of the barrier layer and curtailing the incubation time. 
     SUMMARY OF THE INVENTION 
     An object of this invention is to shorten the incubation time involved during the formation of an embedded Cu interconnection layer through the medium of a barrier layer and, at the same time, exalt the barrier property of a ground layer to Cu. 
     Another object of this invention is to simplify the step for forming an embedded electroconductive layer on a barrier layer. 
     In the formation of an embedded Cu interconnection layer  6 , by using a barrier layer  4  a metal growth promoting layer (a TiN layer containing oxygen at a lower concentration than the barrier layer)  5  jointly as a ground layer  10  as shown in  FIG. 1 , the incubation time can be curtailed without impairing the barrier property. The verification experiment conducted on this point by the present inventor will be described below. 
     FIG.  2 A and  FIG. 2B  are diagrams showing the results obtained respectively of a PVD-TIN layer and a CVD-TiN layer by allowing the layers to stand in an ambience of oxygen for stated durations of time and determining oxygen concentrations in the layers at the ends of these durations. The oxygen concentration mentioned above was detected by measuring the bond energy originating in the Is electron orbit of oxygen in the relevant layer. 
     In the PVD-TIN layer with inferior step coverage, oxygen was detected in significant amounts down to a depth of 625 nm from the surface reached by 2.5 minutes of etchback performed at an etching rate of 250 nm/minute as shown in FIG.  2 A. 
     In contrast, in the CVD-TiN layer with excellent step coverage, substantially no oxygen was detected except on the surface as shown in FIG.  2 B. This contrast may be logically explained by a supposition that since the PVD-TiN layer had small crystal grain particles are compared with the CVD-TiN layer, the former layer permitted easier entrance of oxygen from the ambient air than the latter layer. 
       FIG. 3  is a diagram showing a difference in the amount of growth of Cu (×10 −4  g·cm −2 ) due to a difference in the method of manufacture of a ground layer. A PVD-TIN layer and a CVD-TIN layer were respectively used as ground layers and a Cu layer was formed on each of the ground layers by the CVD method. 
     In the sample using the CVD-TIN layer, deposition of the Cu layer started nearly at the same time that supply of a reaction gas was started during the step of deposition. In the sample using the PVD-TiN layer, substantially no deposition of-the Cu layer occurred even after the elapse of 100 seconds following the start of supply of the reaction gas indicating that this layer had a long incubation time. When hexafluoroacetylacetonate trimethylvinyl silane Cu:Cu (hfac) TMVS is used as a precursor in the deposition of the Cu layer, for example, the precursor is caused to precipitate Cu by the donation of electrons from the surface of the ground layer. When the barrier layer  4  destined to serve as a ground layer has a high oxygen concentration and exhibits low metallicity, therefore, the incubation time is elongated because the donation of electrons from the surface of the barrier layer  4  does not easily occur (S. Cohen et al., Appl. Phys. Lett., Vol. 60, 1992, p. 995). 
     Now, preferred concrete examples of the barrier layer  4  according to this invention will be cited below. 
     Firstly, a Ti-Si-N layer in an amorphous state is used. It excels a crystalline layer in the barrier property relative to Cu. 
     A sputtering method, particularly a collimation sputtering method, or a long throw sputtering method forms one of the methods which are available for forming the Ti-Si-N layer in an amorphous state. The long throw sputtering method requires the interval between a target and a substrate under treatment to be not less than 10 cm. Adoption of this method results in exalting the step coverage because it adds to the parallelism of atoms being sputtered. Another method that is available for the formation of the Ti-Si-M layer in an amorphous state uses a procedure comprising the steps of depositing a TiN layer and then thermally treating the TiN layer in an ambience of SiH, gas. 
     Secondly, a WN x  layer (x=0 to 1) or a TaN x  layer (x=0 to 1) is used. The layer exhibits the barrier property relative to Cu even at 800° C. 
     Thirdly, a TIN layer having an oxidized surface is used. This layer is obtained, for example, by depositing a TIN layer and then thermally treating the TIN layer in an ambience of nitrogen. The trace oxygen entrained by the nitrogen serves to oxidize the surface of the TIN layer. 
     Fourthly, an Al 2 O 3  layer is used. This layer is formed by depositing an Al layer and then thermally treating the Al layer in an oxidizing ambience. 
     The following methods are available for the formation of the TIN layer  5  having a low oxygen concentration. 
     Firstly, a chemical vapor growth method is available. This method can compensate for the thin-wall part of the barrier layer  4  destined to form a ground layer by heightening the step coverage of the layer serving to curtail the incubation time. 
     Secondly, a collimation sputtering method or a long throw sputtering method is available. Adoption of such a sputtering method results in improving to a fair extent the step coverage of the step intended to curtail the incubation time. 
     Such unwanted reactions as the oxidation with the oxygen from the ambient air and the contamination with a defiling substance can be prevented by causing the series of steps ranging from that of deposition of the barrier layer  4  through that of deposition of the Cu layer  6  to be continuously carried out as one process. 
     Now, other methods for forming a ground layer capable of curtailing the incubation time without impairing the barrier property will be described below with reference to FIG.  4  through FIG.  6 . 
       FIG. 4  is a cross section showing the construction of the principle of this invention,  FIG. 5  is a diagram showing the dependency of the amount of growth of the Cu layer on the DMH (dimethyl hydrazine) treatment, and  FIG. 6  is an explanatory diagram of the reducing effect of the DMH treatment manifested on the treated surface. 
     First, the surface of a ground layer  10   a  is reduced to form a layer  7   b  of a low oxygen concentration on the surface of the ground layer  10   a  prior to the growth of the electroconductive layer  6 . As a result, this layer  7   b  acquires exalted metallicity and permits easy supply of electrons from the surface thereof. Thus, the decomposition of the precursor is promoted and the deposition of Cu is accelerated. 
     The event of this process will be explained below with reference to FIG.  5 . 
       FIG. 5  shows the dependency of the amount of growth of Cu (x 10 −4  gcm −2 ) on a substrate obtained when the Cu layer was deposited by the CVD method each on the surface of a PVD-TiN film having undergone a reducing treatment with dimethyl hydrazine (DMH), (CH 3 ) 2 N—NH 2 , and the surface of a PVD-TiN film not having undergone the reducing treatment. 
     In the case of the sample of FIG.  5 ( b ) which had undergone the DMH treatment, deposition of the Cu layer started nearly at the same time that the supply of a reaction gas started at the step of deposition. In contrast, in the case of the sample of FIG.  5 ( a ) which had not undergone the DMH treatment, substantially no deposition of the Cu layer occurred even after the elapse of 100 seconds following the start of the step of deposition, indicating that the substrate had a long incubation time. 
     The amount of growth in this case was determined by means of ICP-AES (inductively coupled plasma-atomic emission spectroscopy. After two minutes&#39; deposition, for example, the sample using the DMH treatment showed a growth of the Cu layer in a thickness of 3000 Å, which was about 8 times the thickness of the Cu layer grown on the sample using no DMH treatment. 
     Specifically, the speed of deposition in the sample using the DMH treatment was 1500 Å/minute, i.e. about 8 times that in the sample using no DMH treatment and about 1.5 times that (about 1000 Å/minute) of the sample obtained by depositing a CVD-TiN film on the layer  7   b  of a low oxygen concentration of the ground layer  10   a  proposed formerly by the present inventor. 
     Now, the effect of the DMH treatment on the reduction of the surface will be described below with reference to FIG.  6 A and FIG.  6 B. 
       FIGS. 6A and 6B  show the results of the determination of oxygen concentration in the Cu layer performed in the sample not having undergone the DMH treatment and the sample having under-gone the DMH treatment respectively prior to the deposition of Cu by measuring the binding energy originating in the  1   s  electron orbit of oxygen in the layer. 
     It is clearly noted from  FIG. 6A  that in the sample using no DMH treatment, oxygen was detected in significant amounts down to a depth of 900 nm from the surface of the grown layer reached by 3.6 minutes of etchback performed at an etching rate of 25 nm/minute, namely down to a depth of 750 nm from the surface of the TiN film reached by 3 minutes of etchback and that the oxygen concentration of the surface of the TIN film was very high. 
     It is clearly noted from  FIG. 6B  that in the sample using the DMH treatment, although oxygen was detected in significant amounts down to a depth of 750 nm from the surface of the TiN film reached by 3 minutes of etchback, the oxygen concentration of the surface of the TIN film was conspicuously low. 
     The reducing treatment given to the surface of the ground layer  10   a , therefore, curtails the incubation time of the electroconductive layer  6  and increases the speed of deposition and the residual oxygen in the interior  7   b  of the ground layer  10   a  secures the barrier property. 
     By performing the reducing treatment as part of the step for elevating the temperature up to the level at which the growth of the electroconductive layer  6  is started, the reduced surface can be retained in a perfect condition because the ground layer  10   a  after the reduction has no possibility of being exposed to the atmosphere. 
     Further by effecting thorough oxidation of the ground layer  10   a  prior to the step for reducing the ground layer  10   a , the barrier property can be exalted and the formation of a deep level caused by the entry of Cu into the silicon substrate and suffered to exert an adverse effect on the life time of the carrier can be repressed. 
     Now, preferred concrete examples of a reducing gas  8  will be cited below. Firstly, dimethyl hydrazine (DMH) is available (T. Obba et al., Proc. Advanced Metallization for VLSI Applications, MRS. p. 211, 1992). This compound is utilized in forming a TiN film by nitriding a Ti film. 
     Secondly, monomethyl hydrazine (MMH) which has the same nitriding action as DMH is available. 
     Thirdly, silane is available. Properly in this case, the thermal treatment is carried out at a relatively low temperature because this compound has the possibility of reacting at a high temperature and producing an amorphous Ti-Si-N film. 
     This invention is also directed to a method for the formation of an embedded electroconductive layer by the steps of depositing a barrier layer  4  on the surface of a depressed part  3  formed in an insulating layer  2 , then growing an electroconductive layer  6  to fill up the depressed part  3  by the chemical vapor growth method using a metallic precursor, which method is characterized by exposing the barrier layer  4  to an etching ambience prior to the growth of the electroconductive layer  6  thereby removing the surface of the barrier layer  4  by etching. 
     When the barrier layer  4  is a CVD-TiN film, an oxygen-containing layer is present only on the surface thereof. By removing the surface of the barrier layer  4  by etching, therefore, the barrier layer  4  is enabled to curtail the incubation time thereof. 
     When the embedded electroconductive layer  6  is utilized as a interconnection layer, the oxygen concentration in the barrier layer  4  must be increased to secure the barrier property. When the electroconductive layer  6  is utilized as a connecting layer (plug) for joining interconnection layers, the oxygen concentration in the barrier layer  4  does not need to be increased because the layer is not required to possess the barrier property. 
     As the etching ambience mentioned above, an ambience which is formed of any one compound selected from among ClF 3 , NF 3 , and BCl 3  is preferably used. 
     Now, preferred concrete examples of the precursor will be cited below. Firstly, a metal complex of Cu is available. For the growth of Cu by the CVD method, it is advantageous to use such a metal complex of Cu as Cu (hfac) TMVS. 
     Secondly, a metal compound of Al is available. For the growth of Al by the CVD method using a precursor, It is proper to use such a metal compound of Al as dimethyl aluminum hydride (DMAH) as the precursor. 
     Thirdly, a combined supply of a metal complex of Cu with a metal compound of Al is available. This supply permits formation of an embedded interconnection layer made of an Al-Cu alloy capable of offering better resistance to electromigration than Al. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  is a cross section showing the construction of the principle of this invention. 
         FIG. 2A  is a diagram showing the oxygen content of a PVD-TIN layer and  FIG. 2B  a diagram showing the oxyget content of a CVD-TIN layer. 
         FIG. 3  is a diagram showing the dependency of the amount of growth of a Cu layer on the substrate to aid in the description of the operation of this invention. 
       FIG.  4 A and  FIG. 4B  are cross sections showing the construction of the principle of this invention. 
         FIG. 5  is a diagram showing the difference in the amount of growth of a Cu layer due to the presence or absence of the DMH treatment on the ground layer. 
       FIG.  6 A and  FIG. 6B  are diagrams showing the effect of reduction manifested by the DMH treatment on the surface. 
         FIG. 7A  to  FIG. 7E  are cross sections showing a process of production according to the first embodiment of this invention. 
       FIG.  8 A and  FIG. 8B  are cross sections showing a process of production according to the second embodiment of this invention. 
         FIG. 9A  to  FIG. 9C  are cross sections showing a process of production according to the third embodiment of this invention. 
         FIG. 10A  to  FIG. 10C  are cross sections showing a process of production according to the fourth embodiment of this invention. 
         FIG. 11A  to  FIG. 11C  are cross sections showing a process of production according to the fifth embodiment of this invention. 
         FIG. 12A  to  FIG. 12D  are cross sections showing a process of production according to the sixth embodiment of this invention. 
         FIG. 13A  to  FIG. 13F  are cross sections showing a process of production according to the seventh embodiment of this invention. 
       FIG.  14 A and  FIG. 14B  are diagrams showing a difference in the oxygen content in a TIN film due to a difference in the method of production. 
         FIG. 15  is a cross section showing part of a process of production according to the eighth embodiment of this invention. 
     
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENT 
     First Embodiment 
     The first embodiment of this invention will be described below with reference to  FIGS. 7A  to  7 E. The reaction devices which are mentioned in the embodiments of this invention are assumed to have inner volumes of 40-80 liters. 
     First, an SiO, layer  12  is deposited in a thickness of 600 nm by the plasma CVD method on a silicon substrate  11  having a 6-inch (about 15 cm) (100) plane  6  as a main surface thereof, a photoresist is applied thereon in a thickness of 0.6 μm and then the SiO 2  layer  12  is covered with a mask of photoresist pattern formed in advance through the steps of exposure and patterning and etched along a wiring pattern by the use of an i ray (365 nm) to form a groove  13  of a width of 300 nm and a depth of 500 nm as shown in FIG.  7 A. 
     In this case, a TEOS (tetra-ethyl-orthosilicate)-SiO 2  layer, an SOG (spin-on glass) layer, or a PSG (phosphosilicate glass) layer may be used for the SiO 2  layer  12 . Otherwise, the SiO 2  layer  12  may be formed by thermally oxidizing the surface of the silicon substrate  11 . 
     Alternatively, this SiO 2  layer  12  may be formed on other insulating layer such as of Si 3 N 4  or on a metallic layer such as of TiN or W instead of being directly formed on the surface of the silicon substrate  11 . 
     Then, a Ti-Si-N film  14  is deposited in a thickness in the range of 10 to 50 nm, preferably in a thickness of 30 nm, by the reactive sputtering method using a target of TiSi 0.6  as shown in FIG.  7 B. The TiSi 0.6 . target used in this case had a diameter of about 30 cm and a thickness of about 3 cm. A mixed gas consisting of Ar and N 2  at a flow volume ratio in the range of 1 to 2, preferably a flow volume ratio of 1, is used. The flow volume of Ar is 10 to 100sccm, preferably  50  sccm and the flow volume of N 2  is 10 to 100 sccm, preferably 50 sccm. These gases are converted into plasma by exposure to an electric power in the range of 0.5 to 1.5 W. The Ti-Si-N film  14  is obtained in an amorphous state as a result. This film  14  exhibits a perfect barrier property to Cu (Iijima et al. Collection of Manuscripts for Lectures, 30a-K10, published at the 42nd Joint Lecture Meeting of Physicists Societies held in the spring of 1995). 
     Subsequently, the Ti-Si-N film  14  is annealed at a temperature in the range of 450 to 600° C., preferably at 600° C. for a period in the range of 20 to 60 minutes, preferably for 30 minutes, for the purpose of improving fast adhesiveness. 
     Then, a CVD-TiN layer  15  is deposited by the CVD method as shown in FIG.  7 C. TiCl 4  supplied at a flow volume in the range of 10 to 30 sccm, preferably at 10 sccm, He supplied at a flow volume in the range of 40 to 80 sccm, preferably at 50 sccm, methyl hydrazine supplied at a flow volume in the range of 0.4 to 0.8 sccm, preferably at 0.7 sccm, and NH 3  supplied at a flow volume in the range of 400 to 800 sccm, preferably at 500 sccm are introduced into a growth chamber, with the pressure inside the growth chamber kept in the range of 50 to 200 mTorrs, preferably at 100 mTorrs. The substrate temperature is kept in the range of 500 to 600° C., preferably at 600° C. By retaining this state for about 40 seconds, the CVD-TiN layer  15  is deposited in a thickness in the range of 10 to 30 nm, preferably in a thickness of 20 nm. A ground layer  20  is completed as a result. 
     This CVD-TiN layer  15  enjoys a decreased incubation time because it has a lower oxygen concentration and exhibits better step coverage than the PVD-TiN layer obtained by the sputtering method. Moreover, it can compensate for the thin-wall part of the amorphous Ti-Si-N film  14  destined to form an underlying barrier layer. 
     Then, a CVD-Cu layer  16  is formed by the CVD method as shown in FIG.  7 D. By using H 2  supplied at a flow volume in the range of 100 to 1000 sccm, preferably at a flow volume of 500 sccm, as a carrier gas, Cu (hfac) TMVS is supplied at a rate in the range of 0.1 to 1.0 g/minute, preferably at a rate of 0.3 g/minute. The pressure in the growth chamber is kept in the range of 100 to 500 mTorrs, preferably at 200 mTorrs. The substrate temperature is kept in the range of 120 to 220° C., preferably at 160° C., to attain the deposition of the CVD-Cu layer  16 . After the elapse of 20 minutes thereafter, the CVD-Cu film  16  is embedded in the groove  13  and, at the same time, superposed on the CVD-TiN film  15  outside the groove  13 . 
     Then, the surface of the substrate is polished by the CMP (chemical mechanical polishing) method. An abrading material based on an alumina powder is used as the slurry. The polishing pressure is kept in the range of 200 to 300 g/cm 2 , preferably at 250 g/cm 2  The rotational rate of the polisher is in the range of 50 to 100 revolutions/minute, preferably at 50 revolutions/minute. When this polishing is continued for 1 to 2 minutes, the unwanted parts of the CVD-Cu layer  16  through the Ti-Si-N film  14 , namely the parts the CVD-Cu layer  16  through the Ti-Si-N film  14  which rise above the height of the groove  13  formed in the SiO 2  layer  12 , are removed. As a result an embedded Cu interconnection layer  16   a  is formed in the groove  13 . 
     The Cu interconnection layer  16   a  thus obtained suffers a signal delay only sparingly because it has low resistivity as compared with the Al interconnection layer. It further enables a semiconductor device to enjoy improved reliability because it spends about twice as much time in fulfilling its duty before sustaining line failure due to electromigration as the Al interconnection layer. 
     Second Embodiment 
     Now, the second embodiment of this invention will be described below with reference to FIG.  8 A and FIG.  8 B. 
     First. In the same manner as in the first embodiment, the groove  13  for wire distribution is formed in a width of 300 nm and a depth of 500 nm in the SiO 2  layer  12  deposited in a thickness of 600 run on the silicon substrate  11  and a WNX layer  14   a  (x =0 to 1) of a thickness in the range of 10 to 30 nm, preferably 30 nm, is deposited thereon as a barrier layer by the RF sputtering method as shown in FIG.  8 A. 
     A TaN x , layer (x =0 to 1) may be used in the place of the WN, layer  14   a  (x =0 to 1). This film exhibits a perfect barrier property to Cu even at such a high temperature as 800° C. (Oku et al., Collection of Manuscripts for Lectures, 30p-K-10, published at the 42nd Joint Lecture Meeting of Physicists Societies held in the spring of 1995). 
     Then, in the same manner as in the first embodiment, the CVD-TIN layer 15 of a thickness of 20 nm is deposited by the CVD method as shown in FIG.  8 B. With a two-ply structure imparted to a ground layer  20   a  destined to support the Cu layer, the barrier property is improved by the WN x , layer  14   a  and, at the same time, the incubation time is curtailed by the CVD-TJA layer  15 . 
     Then, In the same manner as in the first embodiment, a CVD-Cu layer is deposited by the CVD method using Cu (hfac) TMVS as a precursor. Subsequently, an embedded Cu interconnection layer is completed by removing the unwanted parts of the CVD-Cu layer, CVD-TIN layer  15 , and WN x  layer  14   a  by the chemical mechanical polishing method. 
     Third Embodiment 
     Now, the third embodiment of this invention will be described below with reference to  FIG. 9A  to FIG.  9 C. 
     First, in the same manner as in the first embodiment, the groove  13  destined to encase a interconnection layer therein is formed in the SiO 2  layer  12  deposited in a thickness of 600 nm on the silicon substrate  11  as shown in FIG.  9 A. The groove  13  has a width of 300 nm and a depth of 500 nm. Subsequently, A PVD-TIN layer  14   b  Is deposited in a thickness in the range of 10 to 30 nm, preferably in a thickness of 30 nm, by the magnetron sputtering method. 
     Then, the PVD-TiN layer  14   b  is oxidized to form a TiN layer  14   c  having an oxidized surface as shown in  FIG. 9B. N   2  gas is supplied at a flow volume in the range of 20000 to 30000 sccm, preferably at a flow volume of 30000 sccm, and the substrate temperature is kept in the range of 400 to 500° C., preferably at 450° C. In the ambience of N 2 , the layer is annealed for a period in the range of 20 to 60 minutes, preferably for 30 minutes. 
     The oxidation in this case is caused by the trace of oxygen which is entrained in the N 2  gas. The oxidation gives rise to the TiN layer  14   c  which has an oxidized surface of improved barrier property. This layer functions as a barrier layer. 
     Then, in the same manner as in the first embodiment, the CVD-TIN layer  15  is deposited in a thickness of 20 nm by the CVD method as shown in FIG.  9 C. With a two-ply structure imparted to a ground layer  20   b  destined to support the Cu layer, the barrier property is improved by the TiN layer  14   c  and, at the same time, the incubation time is curtailed by the CVD-TiN layer  15 . 
     Then, in the same manner as in the first embodiment, the CVD-Cu layer is deposited by the CVD method using Cu (hfac) TMVS as a precursor. Subsequently, the embedded Cu interconnection layer is formed by removing the unwanted parts of the CVD-Cu layer, the CVD-TiN layer  15 , and the TIN layer  14   c  of an oxidized surface by the chemical mechanical polishing method. 
     Fourth Embodiment 
     Now, the fourth embodiment of this invention will be described below with reference to  FIG. 10A  to  FIG. 10   C.    
     First, in the same manner as in the first embodiment, the groove  13  of a width of 300 nm and a depth of 500 nm destined to encase a interconnection layer therein is formed in the SiO 2  layer  12  deposited in a thickness of 600 nm on the silicon substrate  11  as shown in FIG.  10 A. Subsequently, the PVD-TiN layer  14   b  is deposited in a thickness in the range of 10 to 30 nm, preferably in a thickness of 30 nm, by the magnetron sputtering method. 
     Then, the PVD-TiN layer  14   b  is annealed in an ambience of SiH 4  gas and converted into an amorphous Ti-Si-N layer  14   d  as shown in FIG.  10 B. At this time, the SiH 4  gas is supplied at a flow volume in the range of 50 to 200 sccm, preferably at a flow volume of 100 sccm and the substrate temperature is kept in the range of 400 to 600° C., preferably at 600° C., for a period in the range of 20 to 30 minutes, preferably for a period of 30 minutes. 
     The amorphous Ti-Si-N layer  14   d  in this case exhibits as perfect a barrier property to Cu as the Ti-Si-N layer  14  formed by the sputtering method in the first embodiment. 
     Then, in the same manner as in the first embodiment, the CVD-TIN layer  15  is deposited in a thickness of 20 nm by the CVD method as shown in FIG.  10 C. With a two-ply structure imparted to the ground layer destined to support the Cu layer, the barrier property is improved by the TiN layer  14   d  and, at the same time, the incubation time is curtailed by the CVD-TiN layer  15 . 
     Then, in the same manner as in the first embodiment, the CVD-Cu layer is deposited by the CVD method using Cu (hfac) TMVS as a precursor. Subsequently, the embedded Cu interconnection layer is informed in the groove  13  by removing the unwanted parts of the CVD-Cu layer, the CVD-TIN layer  15 , and the amorphous Ti-Si-N layer  14   d  by the chemical mechanical polishing method. 
     Fifth Embodiment 
     Now, the fifth embodiment of this invention will be described below with reference to  FIG. 11A  to FIG.  11 C. 
     First, in the same manner as in the first embodiment, the groove  13  of a width of 300 nm and a depth of 500 nm destined to encase a interconnection layer therein is formed in the SiO 2  layer  12  deposited in a thickness of 600 nm on the silicon substrate  11  as shown in FIG.  11 A. Subsequently, an Al layer  14   e  is deposited in a thickness in the range of 5 to 10 nm, preferably in a thickness of 10 nm, by the sputtering method. 
     Then, the resultant superposed layers are annealed in the oxidizing ambience  19  to oxidize the Al layer  14   e  and convert it into an Al 2 O 3 , layer  14   f  as shown in FIG.  11 B. The Al 2 O 3  layer  14   f  functions as a barrier to Cu. 
     Then, in the same manner as in the first embodiment, the CVD-TiN layer  15  is deposited in a thickness of 20 nm by the CVD method as shown in FIG.  11 C. With a two-ply structure imparted to the ground layer  20   d  destined to support the Cu layer, the barrier property is improved by the Al 2O   3  layer  14   f  and, at the same time, the incubation time is curtailed by the CVD-TiN layer  15 . 
     Then, in the same manner as in the first embodiment the CVD-Cu layer is deposited by the CVD method using Cu (hfac) TMVS as a precursor. Subsequently, the embedded Cu interconnection layer is formed in the groove  13  by removing the unwanted parts of the CVD-Cu layer, the CVD-TiN layer  15 , and the Al 2 O 3  layer  14   f  by the chemical mechanical polishing method. 
     In the embodiments described above, the RF sputtering method or the magnetron sputtering method is adopted at the step of forming the barrier layers  14 ,  14   a , and  14   b . The formation of the barrier layer does not need to be limited to this method. Any of various other sputtering methods may be used instead. 
     The means to form the CVC-TiN film  15  which is intended to curtail the incubation time in each of the embodiments described above does not need to be limited to the CVD method. For example, the collimation sputtering method or the long throw sputtering method may be adopted instead. 
     The collimation sputtering method is characterized by having interposed between a target and a substrate under treatment a collimator which is provided with passageways resembling the openings in a honeycomb. Owing to the collimator, this method effects the deposition of the CVD-TiN film  15  by exclusively utilizing relatively parallel sputter atom components, namely the sputter atom components which are relatively perpendicular to the substrate under treatment. This method, therefore, provides good step coverage as compared with the ordinary sputtering method and allows the surface of the SiO 2  layer  12  formed in the groove  13  to be covered with a coating of a relatively uniform wall thickness. 
     The long throw sputtering method consists in elongating the interval between a target and a substrate under treatment thereby enabling the deposition to be implemented by exclusive use of relatively parallel sputter atom components. In the present embodiment, the operation using an interval exceeding 10 nm between the target and the substrate under treatment is thought of as conforming to the long throw sputtering method. In this case, the long throw sputtering method provides better step coverage than the ordinary sputtering method. 
     The means to be used for depositing the Ti-Si-N layer  14  in the first embodiment does not need to be limited to the reactive sputtering method. The collimation sputtering method or the long throw sputtering method may be adopted instead for the purpose of improving the step coverage. 
     The embodiments cited above each represent a case of having the groove  13  for the formation of a interconnection layer formed in the SiO 2  layer  12 . Notwithstanding this particular illustration, the present invention can be utilized for a case of having a contact electrode embedded in a contact hole. 
     The embodiments cited above have been each depicted as effecting the deposition of the CVD-Cu layer  16  by adopting Cu (hfac) TMVS as a precursor therefore. This precursor, however, does not need to be limited to the Cu (hfac) TMVS. Other-precursors such as, for example, hexafluoroacetyl acetonate copper [Cu (HFA) 2 ] may be used instead. 
     In each of the embodiments described above, the series of steps ranging from the step of depositing the barrier layer through the step of depositing the CVD-Cu layer may be carried out continuously in a vacuum without exposing the substrate under treatment to the open air. In this case, the component reaction devices involved in the series of steps are connected with a binding chamber. By this arrangement, the interiors of these reaction devices can be prevented from the adverse effects of the oxygen or the defiling substances in the air. 
     This invention imparts to the ground layers  20   a  to  20   d  for the Cu layer  16  a two-ply structure using the barrier layers  14 ,  14   a ,  14   c ,  14   d , and  14   f  capable of preventing diffusion of Cu and the TIN layer  15  of a low oxygen concentration capable of curtailing the incubation time. Owing to this structure, there-fore, the present invention enables a semiconductor device using a Cu interconnection layer of low resistance to be improved in reliability and, at the same time, enhances the throughput of the relevant productional operation. 
     Sixth Embodiment 
     The sixth embodiment of this invention will be described below with reference to  FIG. 12A  to FIG.  12 D. First, the SiO 2  layer  12  is deposited in a thickness of 600 nm by the plasma CVD method on the silicon substrate  11  having a 6-inch (about 15 cm) (100) plane  6  as a main surface thereof as shown in FIG.  12 A. In this case, a TEOS (tetra-ethyl-orthosilicate)-SiO 2  layer or an SOG (spin-on glass) layer may be used for the Si 0   2  layer  12 . Otherwise, the SiO 2  layer  12  may be formed by thermally oxidizing the surface of the silicon substrate  11 . 
     Alternatively, this SiO 2  layer  12  may be formed on other insulating layer such as of Si 3 N 4  or on a metallic layer such as of TiN or W instead of being directly formed on the surface of the silicon substrate  11 . 
     Then, a photoresist is applied thereon in a thickness of 0.6 μm. Thereafter, the SiO 2  layer  12  is covered with a mask of photoresist pattern formed in advance through the steps of exposure and patterning and etched along a wiring pattern 300 nm in width W and 500 nm in depth D by the use of an i ray (365 nm) to form the groove  13  as shown in FIG.  7 A. 
     Then, a TiN film  17  having a thickness in the range of 10 to 50 nm, specifically a thickness of 50 nm, is deposited by the reactive sputtering method using a mixed gas of Ar/N 2 . Ti is used as a target for sputtering. The flow volume ratio of Ar/N 2  is set in the range of 1 to 2, preferably at 1. Ar is supplied at a rate in the range of 10 to 100sccm, preferably at a rate of 50 sccm, and N 2  is supplied at a rate in the range of 10 to 100sccm, preferably at a rate of 50 sccm. After the deposition of the TiN film  17 , the substrate is extracted from the sputtering device. 
     The resultant superposed layers may be annealed in an ambience of N 2  at a substrate temperature in the range of 300 to 600° C., specifically at 450° C. for a period in the range of 10 to 30 minutes such as, for example 30 minutes. By this annealing treatment, the trace amount of oxygen contained in the N 2  gas is added to the TiN film  17  and the oxygen concentration in the TiN film  17  is increased and the barrier property thereof is exalted. 
     Then, dimethyl hydrazine (DMH)  15  is supplied at a flow volume in the range of 10 to 200 sccm, specifically at 20 sccm to adjust the pressure in the treating chamber in the range of 10 to 100mTorrs, specifically at 20 mTorrs. The substrate temperature is kept in the range of room temperature to 500° C., specifically at 400° C., for 60 seconds to reduce the surface of the TiN film  17  and convert the surface layer thereof into a layer  17   b  of a low oxygen concentration. As a result, a ground layer  20   e  composed of an internal layer  17   a  of a high oxygen concentration and a surface layer  17   b  of a low oxygen concentration is formed. 
     Then, the Cu layer  16  is deposited by the CVD method without exposing the TiN film  20   e  to the ambient air as shown in FIG.  12 C. The Cu layer  16  is consequently embedded in the groove  13  and, at the same time, superposed on the ground layer  20   e  outside the groove  13 . At this time, H 2  is supplied as a carrier gas at a flow volume in the range of 100 to 1000 sccm, specifically at 500 sccm and Cu (hfac) TMVS is supplied at a rate in the range of 0.020 to 2.000 g/minute, specifically at 0.165 g/minute. The pressure in the growth chamber is kept in the range of 100 to 1000 mTorrs, specifically at 200 mTorrs. The substrate temperature is kept in the range of 140 to 240° C., specifically at 160° C. for a period of about 20 minutes. 
     Then, the unwanted parts of the Cu layer  16  and the TiN film  20   e , namely the parts of the Cu layer  16  and the TiN film  20   e  which rise above the height of the groove  13 , are removed by the chemical mechanical polishing method using a slurry based on an alumina powder as shown in FIG.  12 D. As a result, the embedded Cu interconnection layer  16   a  is formed in the groove  13 . At this time, the polishing is performed for a period in the range of 1 to 2 minutes, with the polishing pressure kept in the range of 200 to 300 g/cm 2 , preferably at 250 g/cm 2  and the rotational rate of the polisher kept in the range of 50 to 100 revolutions/minute, preferably at 50 revolutions/minute. 
     In the sixth embodiment described above, since the layer  17   b  of a low oxygen concentration is formed by reducing the surface of the TiN film  17  the incubation time involved during the growth of the Cu layer  16  shown in  FIG. 12C  is curtailed to a great extent and the productivity of the relevant operation is enhanced. 
     Since the TiN film  17  is deposited by the sputtering method, namely by the PVD method, the TiN film  20   e  has the layer  17   a  of a high oxygen concentration incorporated in the interior thereof as shown In  FIG. 12D and , therefore, exhibits a perfect barrier property to Cu. 
     Further, the Cu interconnection layer  16   a  suffers a signal delay only sparingly because it has low resistivity as compared with the Al interconnection layer. It also enables a semiconductor device to enjoy improved reliability because it spends about twice as much time in fulfilling its duty before sustaining line failure due to electromigration as the Al interconnection layer. 
     The sixth embodiment described above has been depicted as using the TiN film  17  formed by the sputtering method as a barrier metal. Notwithstanding this particular illustration, it is allowable to use the CVD-TiN film instead. In this case, it is proper for the purpose of improving the barrier property of the TiN film  17  to interject the introduction of oxygen during the course of the CVD process and consequently heighten the oxygen concentration in the intermediate part of the TiN film  17 . When the PVD-TiN film is used, it is permissible for the purpose of enhancing the barrier property thereof to effect thorough oxidation of the TiN film in an oxidizing ambience. When the surface of this thoroughly oxidized TiN film is reduced by the DMH treatment, the N 2  in the DMH acts to deprive the TiN film of oxygen and enrich the N content of the TiN film. 
     Seventh and Eighth Embodiment 
     Now, the method for the formation of an embedded electroconductive layer according to the seventh embodiment of this invention will be described below with reference to  FIG. 13A  to FIG.  13 F. 
     First, a thermally oxidized film  22  of a thickness of 200 nm is formed by thermally oxidizing a silicon substrate  21  having a 6-inch (about 15 cm) (100) plane as a main surface thereof as shown in FIG.  13 A. Subsequently, a plasma TEOS-SiO 2  film  23  of a thickness of 200 nm and an SOG-SiO 2  film  24  of a thickness of 300 nm are sequentially deposited in the order mentioned on the thermally oxidized film  22 . 
     Then, a TiN film  25  of a thickness of 100 nm, an AlCuTi film  26  of a thickness of 600 nm, and a TiN film  27  of a thickness of 100 nm are deposited by the sputtering method. Subsequently, a lower interconnection layer  40   a  of a three-ply structure is formed by patterning the films mentioned above. 
     The proportions of Cu and Ti in the AlCuTi film  26  are respectively 1.0% by weight and not more than 1.0% by weight. 
     Then, a TEOS-SiO 2  film  28  is formed by the plasma CVD method using TEOS so as to have a thickness of 900 nm above the lower interconnection layer  40   a as shown in FIG.  13 B. Subsequently, an SOG-SiO 2  film  29  is formed so as to have a thickness of 100 nm above the lower Interconnection layer  40   a  and give rise to a flat surface. 
     Then, a contact hole  30  measuring 500 nm in diameter and 1000 nm in depth and reaching the lower interconnection layer  40   a  is formed by etching the SOG-SiO 2  film  29  and the TEOS-SiO 2  film  28 . 
     Then, TiCl 4  is supplied at a flow volume in the range of 10 to 20 sccm, specifically 10 sccm, He at a flow volume in the range of 40 to 80 sccm, specifically 50 sccm, monomethyl hydrazine at a flow volume in the range of 0.4 to 0.8 sccm, specifically 0.7 sccm, and NH 3  at a flow volume in the range of 400 to 800 sccm, specifically 500 sccm as shown in FIG.  13 C. The pressure in the growth chamber is kept in the range of 50 to 200 mTorrs, specifically at 100 mTorrs. The substrate temperature is kept in the range of 500 to 600° C., specifically at 600° C. for a period of 100 seconds. As a result, a CVD-TiN film  31  is deposited in a thickness in the range of 10 to 50 nm, specifically 50 nm. 
     Then, DMH  32  is supplied at a flow volume in the range of 10 to 200 sccm, specifically 20 sccm and the pressure in the treating chamber is adjusted in the range of 10 to 100 mTorrs, specifically at 20 mTorrs. By keeping the substrate temperature in the range of room temperature −500° C., specifically at 400° C., for a period of 60 seconds the surface of the CVD-TiN film  31  is reduced. 
     Then, a Cu layer  33  is deposited by the CVD method as shown in  FIG. 13D  without exposing the CVD-TiN film  31  to the ambient air. As a result, the Cu layer  33  is embedded in the contact hole  30 . At this time, H 2  is supplied as a carrier gas at a flow volume in the range of 100 to 1000 sccm, specifically 500 sccm and Cu (hfac) TMVS is additionally supplied at a rate in the range of 0.020 to 2.000 g/minute, specifically 0.165 g/minute. The pressure in the growth chamber is kept in the range of 100 to 1000 mTorrs, specifically 25 at 200 mTorrs. The substrate temperature is kept in the range of 140 to 240° C. specifically at 160° C., for a period of about 20 minutes. 
     Then, the unwanted parts of the Cu layer  33  and the CVD-TiN film  31 , namely the parts of the Cu layer  33  and the CVD-TiN film  31  rising above the height of the contact hole  30 , are removed by the chemical mechanical polishing method using a slurry based on an alumina powder as shown in FIG.  13 E. As a result, an embedded Cu layer or a plug is formed in the contact hole  30 . At this time, the polishing is performed for a period in the range of 1 to 2 minutes, with the polishing pressure kept in the range of 200 to 300 g/cm 2 , preferably at 250 g/cm 2  and the rotational rate of the polisher kept in the range of 50 to 100 revolutions/minute, preferably at 50 revolutions/minute. 
     Then, a TiN film  34  of a thickness of 100 nm, an AlCuTi film  35  of a thickness of 60 nm, and a TIN film  36  of a thickness of 100 nm are deposited by the sputtering method in the same manner as the lower interconnection layer  40   a  as shown in FIG.  13 F. By having these films patterned subsequently, an upper interconnection layer  40   b  of a three-ply structure is formed 
     An increase in the number of plies of the structure is attained by simply repeating the step mentioned above as many times as the additional plies. 
     In the seventh embodiment, since the CVD-TiN film  31  is used as a barrier metal layer, the surface oxidized film is thin as compared with the PVD-TIN film, the reduced TIN film containing no oxygen can be easily obtained, and the incubation time can be curtailed. 
     This situation will be described below with reference to FIG.  14 A and FIG.  14 B. 
     FIG.  14 A and  FIG. 14B  show the results of the determination of oxygen concentration in the CVD-TiN layer and the PVD-TIN layer effected by measuring the bond energy originating in the Is electron orbit of oxygen in the layer. The results indicate that a high oxygen concentration is detected only in the surface part of the CVD-TIN film. 
     In the seventh embodiment, since the barrier property to Cu is retained by the TiN film  27  of the lower interconnection layer  40   a  and the TiN film  34  of the upper interconnection layer  40   b , the CVD-TIN film  31  does not require the barrier property of itself very much and, therefore, the use of the CVD-TIN film is allowed. 
     The CVD-TIN film  31  has a layer of a high oxygen concentration only in the surface region thereof. In the same manner as in the eighth embodiment shown in  FIG. 15 , therefore, the layer of a high oxygen concentration in the surface region can be removed by the etching treatment instead of the reducing treatment shown in  FIG. 13C  so as to curtail the incubation time. In this case, the etching gas to be used may be any member selected from among C 1 F 3  , NF 3 , and BCl 3 . This etching gas may be used as converted into a plasma. Otherwise, activated seeds which are generated by the thermal decomposition of the etching gas may be used. In the other respects, the construction is the same as that utilizing the reducing treatment. 
     In the sixth and the seventh embodiment, the incubation time is curtailed and the throughput in the relevant productional operation is improved because the reducing treatment of the surface layer of the substrate layer or the removal of the surface layer of a high oxygen concentration from the ground layer is carried out while the Cu layer is deposited by the CVD method as described above. 
     Unlike the first through the fifth embodiment, the sixth and the seventh embodiment avoid using the two-ply film consisting of the barrier metal layer and the CVD-TiN film as the ground layer and they further avoid giving a special treatment to the barrier metal layer constituting the ground layer. Thus, the process of production is simplified and the throughput is enhanced. 
     In the sixth and the seventh embodiment described above, the DMH treatment is carried out at 400° C. and the subsequent growth of Cu is carried out after the temperature has fallen to 140° C. or to 160° C. Otherwise, the DMH treatment may be carried out at a low temperature, specifically at a temperature intermediate between room temperature and the temperature for starting the growth of Cu. Thereafter, the growth of Cu may be implemented in the same reaction chamber as is used for the DMH treatment. 
     The reducing treatment is effected by the use of DMH. The medium for the reducing treatment does not need to be limited to DAMN. Monomethyl hydrazine (MMH) may be used instead. Such silanes as SiH 4  and Si 2 H 4  are also usable. When a silane is used, it is preferable to perform the treatment at a fairly low temperature because the silane at a high temperature reacts to form an amorphous Ti-Si-Ti film. 
     Further, the two embodiments contemplate using Cu (hfac) TMVS as a precursor for the Cu layers  16  and  33  to be deposited. The precursor does not need to be limited to Cu (hfac) TMVS. It is permissible to use other precursors such as, for example, hexafluoroacetyl acetonate-Cu:Cu (HFA) 2  instead. 
     They contemplate using monomethyl hydrazine (MMH) as the N source at the step of depositing the CVD-TiN film. It is permissible to use dimethyl hydrazine (DMH) instead. 
     They further contemplate using Cu, a substance excelling in resistance to electromigration, as the material for the embedded electroconductive layer. From the viewpoint of imparting a flat smooth surface to the interconnection layer, however, it is proper to use Al or an Al alloy having Al as a main component as the material for the conductive layer. 
     In the case of the Al interconnection layer, such an Al metal compound as dimethyl aluminum hydride (DMAH) is used as the precursor for the layer. 
     When the Al alloy interconnection layer such as, for example, an Al-Cu alloy layer is used, it is permissible for the purpose of exalting the resistance of the Al embedded electroconductive layer to electromigration to use DMAH and Cu (hfac) TMVS simultaneously as precursors and consequently form an embedded electroconductive layer of an al-cu alloy having a Cu content of not more than 1% by weight.