TW201838956A - Oxynitride thin film and capacitance element - Google Patents

Abstract

A dielectric thin film has a main component including an oxynitride having excellent dielectric property, and a capacitance element includes the dielectric thin film. The dielectric thin film has a main component made of an oxynitride expressed by a compositional formula of AaBbOoNn (a+b+o+n=5), wherein "A" is one or more selected from Sr, Ba, Ca, La, Ce, Pr, Nd, and Na, "B" is one or more selected from Ta, Nb, Ti, and W, and crystalline particles constituting the dielectric thin film are polycrystalline which are not oriented to a particular crystal plane orientation, and further the crystalline particles have columnar shape crystals.

Description

NOx film and capacitor

The present invention relates to a dielectric film having a main composition composed of an oxynitride and a capacitor element including the same.

In recent years, with the miniaturization and high performance of digital devices, capacitive elements using high-performance dielectric films have been sought.

Conventionally, as a dielectric film, a film using a metal oxide material has been widely used. However, the improvement in the characteristics of dielectric thin films brought about by metal oxide materials has reached a limit, and new materials having higher characteristics are being sought. As a material of the dielectric film, an oxynitride can be mentioned. The oxynitride can be represented by ABO ₂ N. However, for example, in the oxynitride represented by the composition formula SrTaO ₂ N, the oxide which becomes the precursor is Sr ₂ Ta ₂ O ₇ . SrTaO ₂ N can also be directly synthesized from a compound containing Sr, Ta, O, and N, and can also be obtained by nitriding Sr ₂ Ta ₂ O ₇ . The relative dielectric constant of Sr ₂ Ta ₂ O ₇ varies depending on the synthesis method, and is approximately 100 (Non-Patent Document 1). On the other hand, the relative dielectric constant of SrTaO ₂ N has a value of several thousand or more (Non-Patent Document 2 and Patent Document 1). That is, the relative dielectric constant is dramatically increased by incorporating nitrogen into the crystal lattice of the oxynitride. Among such oxynitrides, one of the candidates for the new material is a metal oxynitride material in which a part of oxygen atoms in the oxygen octahedron of the perovskite crystal structure is replaced with a nitrogen atom. However, it is difficult to obtain a dielectric film having a metal oxynitride material.

For example, Patent Document 2 and Patent Document 3 describe a method of producing a powder of a perovskite-type oxynitride ABO ₂ N. However, in Patent Document 2 and Patent Document 3, there is no disclosure about obtaining a film using a perovskite-type oxynitride ABO ₂ N.

Further, Non-Patent Document 3 and Non-Patent Document 4 disclose the production of a film made of a perovskite-type oxynitride ABO ₂ N. However, the films obtained in Non-Patent Document 3 and Non-Patent Document 4 are epitaxial films.

The epitaxial film has the disadvantage of spending a lot of time in its manufacture. Non-Patent Document 1 discloses that it takes a long time of 530 hours or less to produce an epitaxial film having a thickness of 20 nm or less. [Prior Art Document] [Patent Literature]

Japanese Unexamined Patent Application Publication No. JP-A No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No.

Non-Patent Document 1: Journal of Materials Science: Materials in Electronics, 11 (2000), p. 575-578 Non-Patent Document 2: Chem. Master., Vol. 16, No. 7, 2004, p.1267-1276 Patent Document 3: Scientific Reports 4. DOI: 10.1038/srep04987 Non-Patent Document 4: KAST 2005 Annual Research Summary 32-33

[Problems to be solved by the invention]

The present invention has been made in view of such circumstances, and an object thereof is to provide a dielectric thin film having a main composition composed of an oxynitride and a dielectric element having excellent dielectric properties and excellent dielectric properties, and a capacitor element including the same. [Technical means for solving the problem]

In the dielectric film according to the present invention, the dielectric film has a main composition composed of an oxynitride represented by a composition formula A _a B _b O _o N _n (a+b+o+n=5), and the above A is Sr. Any one or more of Ba, Ca, La, Ce, Pr, Nd, and Na, wherein B is at least one of Ta, Nb, Ti, and W, and the crystal grains constituting the dielectric thin film are not specific crystals. The polycrystal is oriented in the plane direction and is composed of columnar particles.

The dielectric film according to the present invention can improve the dielectric characteristics by having the above characteristics.

It is preferable that the columnar particles extend in a direction intersecting with the substrate on which the dielectric film is formed.

The composition ratio of the columnar particles penetrating from the surface of the dielectric film to the back surface is preferably 30% or more.

When the composition ratio of nitrogen is measured at a depth position of 1/4 of the surface of the dielectric film in the thickness direction, a depth position of 1/2, and a depth position of 3/4, it is preferable to form nitrogen of the three positions. The rate of change is within ±55%.

Preferably, the above A is Sr, the above B is Ta and/or Nb, and the above n is greater than 0 and less than 1.

The capacitor element related to the present invention has the above dielectric film.

Hereinafter, the present invention will be described based on the embodiments.

Fig. 1 is a schematic view showing a film capacitor (capacitive element) of the present embodiment. In the film capacitor 1 shown in FIG. 1, the lower electrode 12 and the dielectric film 13 are sequentially formed on the substrate 11, and the upper electrode 14 is provided on the dielectric film 13.

The material of the substrate 11 is not particularly limited, but when a Si single crystal substrate is used as the substrate 11, it is excellent in availability and cost. When importance is attached to flexibility, a Ni foil can also be used as a substrate.

The material of the lower electrode 12 and the upper electrode 14 is not particularly limited, and may be used as an electrode. For example, Pt, Ag, Ni, etc. are mentioned. The thickness of the lower electrode 12 is preferably 0.01 to 10 μm. The thickness of the upper electrode 14 is preferably 0.01 to 10 μm.

The dielectric film 13 has a main composition composed of an oxynitride represented by a composition formula A _a B _b O _o N _n (a+b+o+n=5).

A is one or more elements selected from the group consisting of Sr, Ba, Ca, La, Ce, Pr, Nd, and Na. Preferably, A is one or more elements selected from the group consisting of Sr, Ba, La, and Nd. More preferably, A is Sr. By using the above elements as A, a higher capacitance can be obtained. B is one or more elements selected from the group consisting of Ta, Nb, Ti, and W. Preferably, B is one or more elements selected from the group consisting of Ta and Nb. More preferably, B is Ta. By using the above element as B, a dielectric film 13 having less heterophase can be obtained.

Further, in the composition formula A _a B _b O _o N _n , a<1 is preferable. Further, a/b>1 is preferable, and a/b≧1.05 is more preferable. Further, 1>n>0, more preferably 1>n≧0.3, still more preferably 1>n≧0.5. By setting a, b, and n to the above range, good dielectric characteristics can be obtained.

The crystal grains constituting the dielectric film 13 are polycrystals which are not oriented in a specific crystal plane direction. Further, as shown in FIG. 2, the crystal grains constituting the dielectric film 13 are composed of columnar particles X, and the columnar particles X preferably extend in a direction intersecting the substrate 11 on which the dielectric film 13 is formed. Further, as shown in Fig. 2, the columnar particles X preferably penetrate from the surface on the upper electrode 14 side of the dielectric film 13 to the back surface on the substrate 11 side. In the present embodiment, the crystal grains constituting the dielectric thin film 13 are polycrystals that are not oriented in a specific crystal plane direction, and are composed of columnar particles X, whereby dielectric properties are improved.

It is considered that the crystal grains constituting the dielectric thin film 13 are polycrystals which are not oriented in a specific crystal plane direction, and are composed of columnar particles X, whereby nitrogen efficiently enters the crystal grains, and the dielectric thin film is interposed. The electrical characteristics are improved. Usually, the alignment film is formed by a relatively slow deposition rate in order to obtain the orientation, but at such a slow deposition rate, the grain boundary in the film thickness direction which is a diffusion path of nitrogen cannot be sufficiently obtained. In the present embodiment, it is considered that the crystal grains constituting the dielectric film 13 have a columnar particle shape, thereby forming a diffusion path of nitrogen in the film thickness direction, so that nitrogen can efficiently enter the crystal. As a result, in the dielectric thin film of the present embodiment, the relative dielectric constant is improved, and high dielectric characteristics can be obtained.

Further, the composition ratio of the columnar particles X penetrating through the dielectric film 13 to all the crystal grains constituting the dielectric film 13 is preferably 30% or more. The above-described composition ratio is a ratio of the number of columnar particles X penetrating through the number of all crystal grains observed by a transmission electron microscope (TEM) image of the dielectric film 13. When the composition ratio of the columnar particles X that penetrates is set to the above range, the dielectric characteristics are improved.

Further, the nitrogen composition of the dielectric film 13 is preferably a depth position (surface layer side) of 1/4 from the surface thereof in the thickness direction, a depth position of 1/2 (center of the film), and a depth position of 3/4 (substrate side) ), less change. More preferably, the rate of change of the nitrogen composition in each of the depth positions is at most ±55%, more preferably within ±25%, further preferably within ±20%, and particularly preferably within ±16%. By setting the fluctuation rate of the nitrogen composition to the above range at the maximum, the dielectric characteristics are improved. Further, the nitrogen composition in the dielectric film 13 can be confirmed by X-ray photoelectron spectroscopy.

The maximum X of the variation rate is calculated as follows. First, nitrogen compositions of five or more different points were measured at the respective depth positions. Next, the average nitrogen composition at each depth position was determined based on the nitrogen compositions of the above five different points. That is, in calculating the depth position of 1/4 nitrogen average composition X _1, X nitrogen average composition ₂ 1/2 depth position of the average composition of nitrogen depth position of 3/4 or more of the different X 5:00 ₃ . Here, the average value (X ₁ +X ₂ +X ₃ )/3 of the average nitrogen composition at each depth position is defined as the average value X _a of the nitrogen composition of the film. Then, the rate of change X _n '=(X _n -X _a )/X _a (n=1, 2, 3) of each depth position is obtained. That is, the calculated rate of change in the depth position of 1/4 of X ₁ ', the variation rate of 1/2 depth position X _2', the rate of change of the depth position of 3/4 X ₃ '. The rate of change in which the difference between the X ₁ ', X ₂ ', and X ₃ ' and the average value X _a is the largest is the maximum X of the variation rate.

Although the amount of nitrogen is preferably quantified by a nitrided single crystal wafer such as AlN, the sensitivity factor can be calculated from the oxynitride powder having the same composition and the quantitative value can be corrected. In the case of correction by the oxynitride powder, the oxynitride powder may be previously quantified by a pulse heating melt extraction method or the like. In addition, it can also be substituted by the standard in the device.

The thickness of the dielectric film 13 is not particularly limited, but is preferably 10 nm to 2 μm, and more preferably 10 nm to 1 μm.

The dielectric loss tangent (tan δ) of the dielectric film is preferably 60% or less, more preferably 40% or less, further preferably 15% or less, and particularly preferably 10% or less. By setting the dielectric loss tangent (tan δ) to the above range, a dielectric thin film having excellent dielectric properties can be obtained. Further, the dielectric loss tangent (tan δ) of the dielectric film can be measured using an LCR meter at a voltage of 1 V/rms and a frequency of 1 kHz.

The dielectric constant of the dielectric film is preferably 355 or more, more preferably 450 or more, still more preferably 700 or more, and particularly preferably 1110 or more. By setting the relative dielectric constant to the above range, a dielectric thin film having excellent dielectric properties can be obtained. Further, the relative dielectric constant can be measured using an LCR meter at a voltage of 1 V/rms and a frequency of 1 kHz, and is calculated based on the electrostatic capacity, the thickness of the dielectric film, and the electrode area. Method of manufacturing film capacitor 1

Next, a method of manufacturing the film capacitor 1 will be described. In the dielectric thin film 13 having a main composition composed of an oxynitride represented by the composition formula A _a B _b O _o N _n , the case where the A atom is Sr and the B atom is Ta will be described. The same applies to the case of using other kinds of atoms.

The film formation method of the film which finally becomes the dielectric film 13 is not specifically limited. For example, vacuum evaporation method, sputtering method, PLD method (pulse laser evaporation method), MO-CVD (organic metal chemical vapor deposition method), MOD (organometallic decomposition method), sol-gel method , CSD (chemical solution deposition method) and the like. Further, the raw material used for film formation may contain a small amount of impurities, auxiliary components, and the like, but there is no particular problem as long as it does not significantly impair the performance of the film. Further, the dielectric thin film 13 of the present embodiment may contain a small amount of impurities or subcomponents to the extent that the performance is not greatly impaired.

In the film formation method described above, when a film is formed by a method such as a PLD method, a sputtering method, or a CSD method, the finally obtained film is likely to be a polycrystalline film. The CVD method can also perform the synthesis. However, since the number of component elements is large, the composition controllability is higher in the case of the PLD method or the sputtering method. In the present embodiment, a film formation method by the PLD method will be described.

First, as the substrate 11, a Si single crystal substrate is prepared. Next, a film is formed on the Si single crystal substrate in the order of SiO ₂ , TiO _x , and Pt to form a lower electrode 12 made of Pt. The method of forming the lower electrode 12 is not particularly limited. For example, a sputtering method, a CVD method, or the like can be given.

Next, a metal oxide thin film is formed on the lower electrode 12 by a PLD method. In order to expose a part of the lower electrode 12, a metal mask may be used to form a region where a film is not partially formed.

In the PLD method, first, a target containing a constituent element of a target dielectric film is placed in a film forming chamber. Next, a pulsed laser is applied to the surface of the target. The surface of the target is instantaneously evaporated by the intense energy of the pulsed laser. Then, an evaporation material is deposited on the substrate disposed opposite to the target to form a film of the metal oxide.

As the target, for example, a precursor having a composition formula of A ₂ B ₂ O ₇ can be used. The precursor is preferably a perovskite layered compound in which a perovskite unit called a perovskite layer and an O excess layer are alternately deposited.

The type of the target is not particularly limited, and particles obtained by compression-molding the oxynitride powder can also be used. However, since it is necessary to sufficiently manage the amount of N contained, the controllability is good when the particles of A ₂ B ₂ O ₇ are used. Further, it is preferable that each element is evenly distributed in the target, but there may be variations in distribution within a range that does not affect the quality of the obtained dielectric film. Further, the target material is not necessarily required to be one, and a plurality of targets including a part of the constituent elements of the dielectric film can be prepared and used for film formation. The shape of the target is not limited as long as it is a shape suitable for the film forming apparatus to be used. Further, by adjusting the film formation conditions (the gas pressure of oxygen, the gas pressure of nitrogen, the size of the film formation chamber, and the position of the gas introduction tube, etc.), it is possible to control a and b of the finally obtained dielectric film. For example, if a/b of the target is increased, a/b in the film after film formation can be increased.

For example, when the composition of the finally obtained dielectric thin film is Sr _a Ta _b O _o N _n , a sintered body containing Sr ₂ Ta ₂ O ₇ is prepared as a target. Further, by adjusting the film formation conditions (for example, the gas pressure of oxygen, the gas pressure of nitrogen, the size of the film formation chamber, and the position of the gas introduction tube, etc.), it is possible to control a and b of the dielectric film finally obtained.

Film formation conditions are also very important. This is because the metal element evaporated from the target by the pulsed laser is affected by the elements constituting the atmosphere in the film forming chamber, and reaches the film forming surface of the substrate. The atmospheric pressure is widely used in the vicinity of the atmospheric pressure to the atmospheric pressure. The pressure is high. When the vacuum is high, it is easy to obtain a film having high crystallinity. On the other hand, when the atmospheric pressure such as oxygen is high, oxygen or the like is easily obtained. A film with fewer defects. In the case where the plasma is used in combination, the plasma determines the width of the pressure range that can be maintained. Therefore, within the above range, an appropriate pressure may be determined in consideration of crystallinity, defects, and the like. In the case where oxygen and nitrogen are introduced to form an oxynitride film, oxygen hinders the incorporation of nitrogen into the film, and therefore, the pressure is preferably low. Even if oxygen is not introduced, the perovskite structure can be formed by introducing nitrogen activated by the plasma. Further, in the sputtering method, as the atmosphere in the film forming chamber, argon is preferably used in combination.

Further, in the PLD method, in order to crystallize the film-formed metal oxide film, it is preferable to heat the substrate 11 by infrared laser irradiation at the time of film formation. The heating temperature of the substrate 11 at the time of film formation varies depending on the constituent elements and composition of the metal oxide film and the substrate 11, but is preferably 550 to 850 ° C, more preferably 600 to 800 ° C, still more preferably 650 to 750 ° C. By setting the heating temperature of the substrate at the time of film formation to the above range, columnar particles are easily formed. In addition, it is difficult to form voids, and dielectric properties are improved. Further, by setting the temperature of the substrate 11 to an appropriate temperature, the metal oxynitride film is easily crystallized, and generation of cracks generated during cooling can be prevented.

In the film formation, the dielectric film 13 made of a perovskite type oxynitride can be obtained by nitriding by introducing a nitrogen radical. After the metal oxide film is formed into a film, nitrogen radicals may be introduced to carry out nitriding treatment. However, when nitrogen radicals are introduced into the film formation, the amount of nitrogen in the film after film formation can be further increased.

The dielectric film 13 on the substrate may also be subjected to high-speed thermal annealing (RTA) after film formation. The annealing is performed at a temperature higher than the film formation temperature by 100 ° C or lower, more preferably at a film formation temperature or lower, whereby the columnar structure formed at the time of film formation can be maintained. When annealing is performed at a film formation temperature or lower, the XRD pattern of the obtained film is not significantly changed before and after annealing. Therefore, it is presumed that a columnar crystal structure is determined at the time of film formation, and defects are filled during annealing. Stress relaxation and so on.

Finally, the film capacitor 1 can be manufactured by forming the upper electrode 14 on the dielectric film 13. Further, the material of the upper electrode 14 is not particularly limited, and Ag, Au, Cu, or the like can be used. Further, the method of forming the upper electrode 14 is also not particularly limited. For example, it can be formed by a sputtering method or vapor deposition.

Further, an intermediate layer 15 may be provided between the dielectric film 13 and the lower electrode 12 and between the dielectric film 13 and the upper electrode 14. The intermediate layer 15 may be composed of an insulating material or a conductive material. As the insulating material, a compound containing an oxide or a nitride of at least one of aluminum, ruthenium, osmium, and iridium can be used. As the conductive material, Cu, Al, Ni, Au, Ni-Cr, or the like can be used. As a method of forming the intermediate layer 15, a method similar to the method of forming the dielectric thin film 13 described above or the method of forming the lower electrode 12 and the upper electrode 14 can be employed. Further, the intermediate layer 15 can function as an insulating layer, a stress relaxation layer, or a layer for smoothing the unevenness of the electrode surface. The intermediate layer 15 may be between the dielectric film 13 and the lower electrode 12 and between the dielectric film 13 and the upper electrode 14, or may be either. In the case where there are a plurality of intermediate layers, each intermediate layer may also have a different function. The thickness of the intermediate layer 15 is preferably 20% or less, more preferably 10% or less, of the thickness of the dielectric film 13.

The dielectric film of the present embodiment can be used, for example, as a capacitor capable of voltage tuning, a dielectric layer of a high-density capacitor device such as a decoupling film capacitor, or the like.

The capacitor element of the present embodiment is an element having excellent dielectric properties using the dielectric thin film of the present embodiment, and includes a capacitor, a thermistor, a filter, a duplexer, a resonator, a transmitter, an antenna, and a piezoelectric element. Components, transistors, ferroelectric memory, etc. The dielectric film of the present embodiment is suitably used for a capacitor element which requires a high dielectric property.

As a capacitor element of the present embodiment, for example, a method of manufacturing a capacitor includes a method of forming a high-tuning device structure having an appropriate electrode on a substrate. The configuration of the high-tuning device is not particularly limited. For example, a SAW duplexer, a switch using RF-MEMS, a piezoelectric drive type MEMS air gap varactor, and a fixed (low tuning) high density may be used. A device structure in which a film capacitor, a TFBAR circuit, a resistor, an inductor, an oxide-based TFT, and a sensor are integrated with other thin film devices.

The embodiments of the present invention have been described above, but the present invention is not limited to the embodiments, and various modifications may be made without departing from the spirit and scope of the invention. [Examples]

Hereinafter, the present invention will be described based on more detailed examples, but the present invention is not limited to these examples. Example 1

First, SrCO ₃ powder and Ta ₂ O ₅ powder are prepared as a raw material of a sintered body of Sr ₂ Ta ₂ O ₇ used as a target for film formation. The SrCO ₃ powder and the Ta ₂ O ₅ powder were weighed so that the molar ratio of Sr/Ta became 1.

Next, the SrCO ₃ powder and the Ta ₂ O ₅ powder were mixed by a wet ball mill using an ethanol solvent for 16 hours to obtain a mixed slurry.

Next, the mixed slurry was dried at 80 ° C for 12 hours using a constant temperature dryer to obtain a mixture.

Next, the above mixture was slightly pulverized in a mortar and placed in a ceramic crucible. Then, heat treatment was performed at 1000 ° C for 2 hours in an air atmosphere using an electric furnace to obtain a burnt product.

Next, the burned material was again mixed by a wet ball mill using an ethanol solvent for 16 hours to obtain a slurry after calcination.

The obtained calcined slurry was dried at 80 ° C for 12 hours using a constant temperature dryer to obtain a mixture after calcination.

To the above-mentioned calcined mixture, a polyvinyl alcohol solution as a binder was added and mixed to obtain a granulated product. The amount of the polyvinyl alcohol solution added was set to 0.6% by weight based on 100% by weight of the pulverized product.

The granulated product was molded into a cylindrical shape having a diameter of about 23 mm and a height of about 9 mm to obtain a molded product. The molding method is set to CIP molding.

The molded product was fired at 1400 ° C for 2 hours in an air atmosphere using an electric furnace to obtain a sintered product. Further, the upper surface and the lower surface of the sintered body were mirror-polished to obtain a film formation target having a height of 5 mm. Further, it was confirmed that the relative density of the obtained film formation target was 96 to 98%.

The film formation target obtained as described above is placed in a film forming apparatus, and a Si substrate is provided so as to face the film formation target. As the Si substrate, a substrate having a Pt film as a lower electrode on its surface was used.

In Example 1, a pulsed laser was irradiated at a frequency of 10 Hz by a PLD method, and a film was formed so as to have a thickness of 500 nm. At this time, nitrogen is not introduced into the film forming chamber, and only oxygen is introduced to form a dielectric oxide film. Further, in the film formation, plasma was irradiated for 0.5 hour. The film formation temperature was set to 700 °C. Immediately after the film formation, nitrogen radicals were introduced, and nitriding treatment was carried out for 30 minutes to obtain a dielectric film sample. The obtained dielectric film sample was evaluated as follows. Evaluation of polycrystalline film and its orientation

The obtained sample was subjected to XRD measurement using a fully automatic horizontal multi-target X-ray diffraction apparatus SmartLab manufactured by Rigaku Co., Ltd., and it was confirmed from the XRD pattern whether or not the alignment film was oriented to a specific plane and whether or not it had polycrystallinity. In the case of an oriented film having polymorphism and not oriented on a specific plane, it was evaluated as "good", and when it was not in the case of polycrystalline or in the case of an oriented film, it was evaluated as "poor". Further, the composition of the oxynitride contained in the obtained film sample was measured by photoelectron spectroscopy using PHI Quantera II ^TM manufactured by ULVAC-PHI, Inc. The composition in the depth direction of the film was quantified while performing Ar etching. Determination of the rate of change of nitrogen composition

The obtained sample was measured at a depth of 1/4 of the surface of the film in the thickness direction, and a nitrogen composition (atm%) of five different points was measured by an X-ray photoelectron spectroscopy apparatus, and the average was calculated. The nitrogen composition (atm%) was measured in the same manner at a depth position of 1/2 from the surface of the film in the thickness direction and a depth position of 3/4, and the average was calculated. The maximum rate of change is calculated based on these averages. The results are shown in Table 1. The presence or absence of voids and evaluation of columnar particles

For the obtained sample, observation of the film cross section was carried out using a scanning electron microscope (SEM). From the SEM image, the presence or absence of voids of 30 nm or more in the observation field of three fields of view of 1.2 μm × 1.5 μm was confirmed. Further, the presence or absence of columnar particles was confirmed based on the TEM image obtained using a transmission electron microscope (TEM). Further, in the case of having columnar particles, it is confirmed whether or not the columnar particles extend in a direction crossing the substrate. Then, based on the TEM image, the ratio of the penetrating columnar particles was calculated. The results are shown in Table 1. Further, the TEM image obtained in Example 1 is shown in Fig. 3. Determination of dielectric properties (tan δ and relative dielectric constant)

The electrostatic capacitance and tan δ of the sample were measured using an LCR meter at a voltage of 1 V/rms and a frequency of 1 kHz. Then, the relative dielectric constant is calculated based on the thickness of the film, the electrode area, and the electrostatic capacitance. Crystal structure

The crystal structure of the obtained sample was confirmed by XRD measurement. Example 2

In Example 2, a dielectric oxide film was formed into a film by a PLD method so as to have a thickness of 1000 nm. Further, nitrogen radicals are introduced during film formation to carry out nitriding treatment, but nitrogen radicals are not introduced after film formation. Other conditions were carried out in the same manner as in Example 1 to obtain a dielectric film sample. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. In addition, the TEM image is shown in Fig. 4. Example 3

In Example 3, a dielectric oxide film was formed into a film by a PLD method so as to have a thickness of 500 nm. The film formation temperature was set to 600 °C. Other conditions were carried out in the same manner as in Example 1 to obtain a dielectric film sample. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Example 4

A dielectric film sample was obtained in the same manner as in Example 1 except for the following. In other words, in Example 4, La ₂ O ₃ powder and TiO ₂ powder were prepared as a raw material of a La ₂ Ti ₂ O ₇ sintered body used as a target for film formation. The La ₂ O ₃ powder and the TiO ₂ powder were weighed so that the molar ratio of La/Ti became 1. Further, the dielectric oxide film was formed into a film by a PLD method so as to have a thickness of 500 nm. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Example 5

A dielectric film sample was obtained in the same manner as in Example 1 except for the following. In other words, in Example 5, BaCO ₃ powder and Ta ₂ O ₅ powder were prepared as a raw material of a sintered body of an oxide having a molar ratio of 1 in Ba/Ta used as a target for film formation. The BaCO ₃ powder and the Ta ₂ O ₅ powder were weighed in such a manner that the molar ratio of Ba/Ta was 1. Further, the dielectric oxide film was formed into a film by a PLD method so as to have a thickness of 500 nm. Since there is no composition of Ba ₂ Ta ₂ O ₇ , even if the molar ratio of Ba/Ta of the target sintered body is adjusted to be 1, it is difficult for the molar ratio of the film obtained by the film formation conditions. Transfer target composition. Therefore, a sample having a molar ratio of Ba/Ta of 1 was measured for the partial pressure at the time of film formation, and the same evaluation as in Example 1 was carried out. The results are shown in Table 1. Example 6

In the same manner as in Example 1, except that the film formation temperature was changed to 500 ° C, a dielectric film sample was obtained. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Example 7

In the same manner as in Example 1, except that the film formation temperature was changed to 850 ° C, a dielectric film sample was obtained. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Comparative example 1

In Comparative Example 1, a dielectric film sample was obtained in the same manner as in Example 2 except that the film formation temperature was changed to 400 °C. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Comparative example 2

In Comparative Example 2, a dielectric film sample was obtained in the same manner as in Example 2 except that the film formation temperature was changed to 300 °C. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1. Comparative example 3

In Comparative Example 3, a dielectric film sample was obtained in the same manner as in Example 1 except that the film formation temperature was changed to 900 °C. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 1.

[Table 1]

According to the TEM images of Tables 1 and 3 and 4, it was confirmed that in Examples 1 to 7, polycrystals having no voids and not oriented in a specific crystal plane direction were obtained, and the direction intersecting with respect to the substrate was obtained. The dielectric film sample composed of the elongated columnar particles had a maximum variation rate of N composition of ±55% or less and uniformity in the film thickness direction. On the other hand, in the dielectric thin film sample of Comparative Example 1, voids were observed, and columnar particles were not observed. In the film sample of Comparative Example 2, no void was observed, but no crystal structure was observed, and columnar particles were not observed. Further, in Comparative Examples 1 and 2, no nitrogen was detected. In the film sample of Comparative Example 3, columnar particles were not observed, and the maximum variation rate of the N composition exceeded ±55%. Example 8

In the same manner as in Example 1, except that the plasma irradiation time at the time of film formation was further extended, a dielectric film sample was obtained. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 2. Further, as for the crystal structure, the result of "no peak shift" was obtained as compared with Example 1. The "peakless movement" means that the peak position of the pattern obtained by the X-ray diffraction does not move, and the size of the crystal lattice is not changed as compared with the first embodiment regardless of the state of nitrogen N. Example 9

In the same manner as in Example 1, except that the plasma irradiation time at the time of film formation was further extended, a dielectric film sample was obtained. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 2. Further, in the crystal structure, as in the eighth embodiment, the result of "peakless movement" was obtained as compared with the first embodiment. Examples 10 and 11

In Examples 10 and 11, a dielectric film sample was obtained in the same manner as in Example 1 except that the frequency of the pulse laser and the film formation atmosphere were changed. Evaluation was carried out in the same manner as in Example 1. The results are shown in Table 2. Further, as for the crystal structure, the result of "peakless movement" was obtained as compared with Example 2. That is, in Examples 10 and 11, it was found that the size of the crystal lattice did not change as compared with Example 2, regardless of the state of nitrogen N.

[Table 2]

1‧‧‧ Film Capacitors

11‧‧‧Substrate

12‧‧‧ lower electrode

13‧‧‧Dielectric film

14‧‧‧Upper electrode

15‧‧‧Intermediate

X‧‧‧ columnar particles

Fig. 1 is a schematic view showing a film capacitor according to an embodiment of the present invention. Fig. 2 is a schematic view showing the shape of columnar particles in the dielectric film of one embodiment of the present invention in a broken line. Fig. 3 is a TEM image of the dielectric film sample of Example 1, and the broken line indicates the shape of the particles. Fig. 4 is a TEM image of the dielectric film sample of Example 2, and the broken line indicates the shape of the particles.

Claims (6)

A dielectric film characterized in that the dielectric film has a main composition composed of an oxynitride represented by a composition formula A _a B _b O _o N _n , wherein a+b+o+n=5, and the above A is Sr, Ba Any one or more of Ca, La, Ce, Pr, Nd, and Na, wherein B is at least one of Ta, Nb, Ti, and W, and crystal grains constituting the dielectric thin film are not directed to a specific crystal plane The oriented polycrystal is composed of columnar particles. The dielectric film according to claim 1, wherein the columnar particles extend in a direction intersecting the substrate on which the dielectric film is formed. The dielectric film according to claim 2, wherein a composition ratio of the columnar particles penetrating from the surface of the dielectric film to the back surface is 30% or more. The dielectric film according to any one of claims 1 to 3, wherein a depth position of 1/4 of a distance from the surface of the dielectric film in the thickness direction, a depth position of 1/2, When the composition ratio of nitrogen is measured at a depth position of 3/4, the rate of change of the nitrogen composition at the three positions is at most within ±55%. The dielectric thin film according to any one of claims 1 to 3, wherein the A is Sr, the B is Ta and/or Nb, and the n is greater than 0 and less than 1. A capacitor element according to any one of the first to fifth aspects of the invention.