JP2009242199A - Piezoelectric ceramic and laminated piezoelectric element using it - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a piezoelectric ceramic having sufficient piezoelectric characteristics even when baked at a low baking temperature so that internal electrodes with a high containing ratio of Ag are simultaneously baked. <P>SOLUTION: The piezoelectric ceramic includes a complex oxide having a compositional formula (1): (Pb<SB>1-β</SB>Me<SB>β</SB>)<SB>α</SB>[(Cu<SB>1/3</SB>Nb<SB>2/3</SB>)<SB>a</SB>Ti<SB>b</SB>Zr<SB>c</SB>]O<SB>3</SB>(wherein, Me is at least one kind of elements selected from the group consisting of Ca, Sr and Ba; and α, β, a, b and c are satisfied with such relations as 0.99≤α≤1.005 (2), 0≤β<0.1 (3), 0.005≤a≤0.10 (4), 0.40≤b≤0.50 (5), 0.40≤c≤0.58 (6), and a+b+c=1 (7)) as a main ingredient. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a piezoelectric ceramic and a laminated piezoelectric element using the same.

Piezoelectric elements are used in a wide range of electronic components such as actuators, transformers, and ultrasonic motors. A piezoelectric ceramic used for such a piezoelectric element is required to have a large piezoelectric characteristic, particularly a piezoelectric strain constant. Examples of the piezoelectric ceramic satisfying such characteristics include lead titanate (PbTiO ₃ ), lead zirconate (PbZrO ₃ ), and lead zinc niobate (Pb (Zn _1/3 Nb _2/3 ) O ₃ ). There are known those composed of complex oxides of these, and those composed of complex oxides in which elements of these composite oxides are partially substituted.

For _{example, (Pb 1-x M x} ) in _{n {A1 y A2 (1-} y)} Ti b Zr c O 3 composition, piezoelectric ceramics having various elements as M, A1, A2 etc. (piezoelectric ceramic) Is disclosed (see Patent Document 1).
Japanese Patent No. 3874229

  Conventional piezoelectric ceramics need to be fired at a high temperature in order to obtain high characteristics. Therefore, for example, when a laminated piezoelectric element is manufactured by simultaneously firing a piezoelectric ceramic material composition (piezoelectric ceramic composition) and an internal electrode, a noble metal (Pt) having a high melting point that can withstand high-temperature firing. , Pd, etc.).

  However, since these internal electrode materials are extremely expensive, it has been a major factor that hinders the cost reduction of multilayer piezoelectric elements that are being applied to various electronic components in recent years. In order to reduce the price, it is desirable to replace the noble metal with relatively inexpensive Ag or the like. However, since Ag has a lower melting point than noble metal, the higher the content ratio of Ag, the lower the temperature at which it can be fired. There was a tendency that sufficient piezoelectric characteristics could not be obtained. In the piezoelectric ceramic described in Patent Document 1 described above, when the firing temperature is low due to simultaneous firing with the internal electrode having a high Ag content ratio, piezoelectric characteristics are often lowered without being sufficiently fired. There is a need for a piezoelectric ceramic having a composition that can surely be fired at a low temperature.

  Therefore, the present invention has been made in view of such circumstances, and an object thereof is to provide a piezoelectric ceramic capable of obtaining sufficient piezoelectric characteristics even when an internal electrode having a high Ag content ratio is fired simultaneously. And Another object of the present invention is to provide a laminated piezoelectric element having a piezoelectric layer made of such a piezoelectric ceramic.

  As a result of intensive studies to achieve the above object, the present inventors have found that a specific third component is further included in the composition of the lead titanate (PT) -lead zirconate (PZ) piezoelectric ceramic. With such a composition, it has been found that sufficient piezoelectric characteristics can be obtained even by low-temperature firing, and the present invention has been completed.

That is, the piezoelectric ceramic according to the present invention includes a composite oxide represented by the following composition formula (1) as a main component.
_{(Pb 1-β Me β)} α [(Cu 1/3 Nb 2/3) a Ti b Zr c] O 3 ... (1)
[In the formula (1), Me is at least one element selected from the group consisting of Ca, Sr and Ba, and α, β, a, b and c are the following formulas (2), (3 ), (4), (5), (6), and (7).
0.99 ≦ α ≦ 1.005 (2)
0 ≦ β ≦ 0.1 (3)
0.005 ≦ a ≦ 0.10 (4)
0.40 ≦ b ≦ 0.50 (5)
0.40 ≦ c ≦ 0.58 (6)
a + b + c = 1 (7)]

  The piezoelectric ceramic of the present invention has a main composition in which a specific combination of elements of Cu and Nb is further added to the PT-PZ-based composition, and these elements have a specific composition as described above. It is included so as to have a composition ratio. Therefore, sufficient piezoelectric properties (especially piezoelectric strain constants) can be obtained even when the material is formed by low-temperature baking, specifically, low-temperature baking that allows simultaneous firing with an internal electrode having an Ag content exceeding 85%. ). Therefore, according to such a piezoelectric ceramic, it is possible to obtain a multilayer piezoelectric element that is inexpensive and has sufficient piezoelectric characteristics since the content ratio of Ag in the internal electrode is high.

  The present invention also provides a multilayer piezoelectric element comprising a piezoelectric layer comprising the piezoelectric ceramic of the present invention and an electrode (internal electrode) layer having an Ag content of 85% by mass or more. Such a multilayer piezoelectric element of the present invention is inexpensive because the Ag content is 85% by mass, and even if formed by co-firing with such an electrode layer, the piezoelectric ceramic of the present invention described above is used. Since the piezoelectric layer is provided, excellent piezoelectric characteristics can be exhibited.

  According to the present invention, it is possible to provide a piezoelectric ceramic capable of obtaining sufficient piezoelectric characteristics even when an internal electrode having a high Ag content ratio is fired simultaneously. In addition, according to the present invention, it is possible to provide a multilayer piezoelectric element including a piezoelectric layer made of such a piezoelectric ceramic.

  Hereinafter, preferred embodiments of the present invention will be described with reference to the drawings as necessary.

  FIG. 1 is a diagram schematically showing a cross-sectional configuration of a multilayer piezoelectric element according to a preferred embodiment. As shown in FIG. 1, the multilayer piezoelectric element 10 is a multilayer in which the internal electrodes 1 a and the internal electrodes 1 b are alternately arranged, and the piezoelectric layer 2 is sandwiched between the internal electrodes 1 a and 1 b. It has a structure. In addition, a protective layer 3a and a protective layer 3b are provided in the outermost layer of this laminated structure. Furthermore, a pair of external electrodes 4 are provided on both end faces along the stacking direction of the stacked structure. The internal electrode 1a and the internal electrode 1b are connected to the external electrodes 4 on different sides.

  In the multilayer piezoelectric element 10 having such a configuration, the thickness of the piezoelectric layer 2 is preferably 1 to 200 μm, more preferably 20 to 150 μm, and further preferably 50 to 100 μm. Moreover, the thickness of the internal electrode 1a and the internal electrode 1b is preferably 0.5 to 20 μm, and more preferably 1.0 to 10 μm.

  The internal electrodes 1a and 1b are not particularly limited as long as they are made of a material used as an internal electrode of the multilayer piezoelectric element, and are made of, for example, an alloy containing Ag, Pd, Pt, or Ag. In particular, in the multilayer piezoelectric element 10 of the present embodiment, the internal electrodes 1a and 1b are preferably made of a material containing 85% by mass or more of Ag. Specifically, an alloy containing 85% by mass or more of Ag (for example, , Ag—Pd alloy, Ag—Pt alloy, etc.), or those consisting of Ag alone are preferable. In the laminated piezoelectric element 10 of the present embodiment, since the piezoelectric layer 2 is formed from a piezoelectric ceramic as will be described later, the material of the internal electrodes 1a and 1b having such a high Ag ratio can be used simultaneously. Firing is possible.

  On the other hand, the piezoelectric layer 2 is composed of a piezoelectric ceramic having a specific composition. Hereinafter, a piezoelectric ceramic suitable as a constituent material of the piezoelectric layer 2 will be described.

The piezoelectric ceramic of this embodiment includes a composite oxide represented by the following composition formula (1) as a main component.
_{(Pb 1-β Me β)} α [(Cu 1/3 Nb 2/3) a Ti b Zr c] O 3 ... (1)
[In the formula (1), Me is at least one element selected from the group consisting of Ca, Sr and Ba, and α, β, a, b and c are the following formulas (2), (3 ), (4), (5), (6), and (7).
0.99 ≦ α ≦ 1.005 (2)
0 ≦ β ≦ 0.1 (3)
0.005 ≦ a ≦ 0.10 (4)
0.40 ≦ b ≦ 0.50 (5)
0.40 ≦ c ≦ 0.58 (6)
a + b + c = 1 (7)]

  The composite oxide as the main component has a so-called perovskite structure. Pb and Me in the composite oxide represented by the above formula (1) are located at the A site of the perovskite structure. On the other hand, Cu, Nb, Ti, and Zr are located at the B site of the perovskite structure. In the piezoelectric ceramic according to the present embodiment, it is preferable that 95% by mass or more of the composite oxide represented by the above formula (1) as the main component is contained in the total amount of the composition, and 98.0 to 99.9 mass. % Is more preferable. When the composite oxide is contained at such a ratio, sufficient piezoelectric characteristics (particularly piezoelectric strain constant) can be obtained.

  Α indicating the proportion of the A-site element in the composite oxide represented by the above formula (1) is 0.99 ≦ a ≦ 1.005. When the ratio α of the A-site element is less than 0.99 or exceeds 1.005, the piezoelectric strain constant decreases. From the viewpoint of obtaining a good piezoelectric strain constant even when firing at a low temperature, the ratio α of the A site element is preferably 0.993 ≦ a ≦ 1.002, and 0.996 ≦ a ≦ 1. More preferably, it is .000.

  In the composite oxide represented by the above formula (1), a part of Pb that is an A site element may be substituted by an element represented by Me (Ca, Sr, Ba). Such substitution may further improve the piezoelectric strain constant. However, if the amount of substitution is too large, the piezoelectric strain constant tends to decrease rather. Therefore, the substitution amount β by Me is 0.1 or less, more preferably 0.005 ≦ b ≦ 0.08, and further preferably 0.007 ≦ b ≦ 0.05. Note that the substitution element represented by Me may be a plurality of types of Ca, Sr, and Ba. In this case, it is preferable that the total substitution amount of each element satisfies the β value described above.

Of the B site elements in the complex oxide represented by the above formula (1), a representing the ratio of Cu and Nb is 0.01 ≦ a ≦ 0.10. This a affects the firing temperature. When this value is less than 0.01, sufficient piezoelectric characteristics cannot be obtained at a low firing temperature. On the other hand, when the ratio exceeds 0.10, the ratio of Pb (Cu _1/3 Nb _2/3 ) O _{3 having} low ferroelectricity increases, so that the piezoelectric characteristics deteriorate. From the viewpoint of obtaining sufficient sinterability at a low firing temperature, the ratio a between Cu and Nb is preferably 0.007 ≦ a ≦ 0.07, and more preferably 0.01 ≦ a ≦ 0.05. preferable.

  Further, among the B-site elements, b, which is the proportion of Ti, and c, which is the proportion of Zr, are in the following ranges from the viewpoint of obtaining a good piezoelectric strain constant. That is, the Ti ratio b is 0.40 ≦ y ≦ 0.50. The ratio c of Zr is 0.40 ≦ z ≦ 0.58. By setting the proportions of Ti and Zr within these ranges, a large piezoelectric strain constant can be obtained in the vicinity of the morphotropic phase boundary (MPB). In order to obtain such an effect even better, the Ti ratio b is preferably 0.43 ≦ b ≦ 0.48, and more preferably 0.45 ≦ b ≦ 0.47. On the other hand, the ratio c of Zr is more preferably 0.47 ≦ c ≦ 0.54, and further preferably 0.51 ≦ c ≦ 0.53.

  The piezoelectric ceramic according to the present embodiment contains the composite oxide having the above-described composition as a main component, but further includes other subcomponents as long as it does not deteriorate the characteristics such as low-temperature firing. You may go out. However, the composite oxide can exhibit sufficient piezoelectric characteristics when it is fired at a low temperature, even if it does not contain a subcomponent.

  As subcomponents that may be included in the piezoelectric ceramic, for example, Ta, Sb, Nb, W, Sn, Dy, Gd, Yb, Er, Y, Bi, V, Hf, Cr, Mo, Tb, Ho, Examples thereof include oxides of metal elements such as Tm. These may be included in combination of a plurality of types.

  Next, a method for manufacturing the multilayer piezoelectric element 10 having the above-described configuration will be described.

First, starting materials for a composite oxide that is a main component of a piezoelectric ceramic for obtaining the piezoelectric layer 2 are prepared and weighed so that a composite oxide having a desired composition can be obtained. Examples of the starting material include oxides of each constituent element of the composite oxide and powders such as carbonates or oxalates that can be changed to these oxides by firing. Specific examples of the oxide include PbO, TiO ₂ , ZrO ₂ , CuO, Nb ₂ O ₅ , SrO, BaO, and CaO. As the starting material powder, those having an average particle size of about 0.5 to 10 μm are preferable.

  When the piezoelectric ceramic further includes a subcomponent in addition to the composite oxide, the subcomponent starting material may be added to the composite oxide starting material. Examples of the starting material for the accessory component include oxides of the metal elements as described above. In addition, the starting material of a subcomponent can also be added after calcination mentioned later.

  Subsequently, these starting materials are mixed, and if necessary, wet pulverization and mixing are performed to obtain a raw material mixture. Such wet grinding and mixing can be performed using, for example, a ball mill.

  Then, this raw material mixture is dried, and calcined, for example, by performing a heat treatment at a temperature of 750 to 950 ° C. for 1 to 6 hours. This pre-baking may be performed in the air, or may be performed in an atmosphere having a higher oxygen partial pressure or in a pure oxygen atmosphere than in the air. The obtained calcined product is wet-ground and mixed by a ball mill or the like to obtain a calcined powder containing a main component and, if necessary, a subcomponent. By such preliminary firing, a composite oxide is formed from the starting material of the main component, and a piezoelectric ceramic composition capable of forming a piezoelectric ceramic by firing is obtained. This piezoelectric ceramic composition has substantially the same composition as the fired piezoelectric ceramic.

  Next, an organic binder, an organic solvent, an organic plasticizer, and the like are added to the piezoelectric ceramic composition thus obtained, and the mixture is mixed for about 20 hours by a ball mill or the like to obtain a piezoelectric paste.

  In addition to such a piezoelectric paste, an electrode paste for forming the internal electrodes 1a and 1b is prepared. The electrode paste is obtained, for example, by adding a binder, an organic solvent, or the like to the constituent metal powder of the internal electrodes 1a and 1b as described above. The metal content in the electrode paste is preferably 40% by mass or more, and more preferably 50 to 60% by mass. If the metal content is less than 40% by mass, the resulting internal electrodes 1a and 1b may have insufficient conductivity.

  Then, the piezoelectric paste is applied onto a base film made of polyethylene terephthalate (PET) or the like by, for example, a doctor blade method to obtain a piezoelectric green sheet for forming the piezoelectric layer 2. Next, an electrode paste is applied on the piezoelectric green sheet by a screen printing method or the like to obtain a laminated sheet in which an electrode paste layer is formed on the piezoelectric green sheet. At this time, the electrode paste layer is formed corresponding to the shape of the internal electrodes 1a and 1b.

  Thereafter, a plurality of the obtained laminated sheets are stacked so that the electrode paste layers and the piezoelectric green sheets are alternately arranged, and the piezoelectric layers to be the protective layers 3a and 3b are formed above and below the laminated structure thus obtained. Stack green sheets further to get green chips. The green chip manufacturing method is not necessarily limited to this, and the piezoelectric paste and the electrode paste may be alternately and repeatedly applied.

  The green chip thus obtained is subjected to predetermined heating to remove the binder and the organic solvent contained in the middle of each pace. The binder removal is preferably performed under conditions such that the firing of the piezoelectric ceramic composition in the piezoelectric paste does not proceed. For example, the binder removal can be performed at 300 to 650 ° C. for about 0.5 to 50 hours.

  Thereafter, the green chip after debinding is subjected to a firing process (main firing) in, for example, a sealed container. In this main firing process, the piezoelectric green sheet (the piezoelectric ceramic composition in the piezoelectric green sheet) and the electrode paste layer are fired simultaneously, and the piezoelectric layer 2 composed of the piezoelectric ceramic from the piezoelectric green sheet is transferred from the electrode paste layer to the internal electrode. 1a and 1b are formed, respectively. Further, the protective layers 3a and 3b are formed from a piezoelectric green sheet laminated on the outermost layer of the green chip.

  The firing temperature in the main firing is preferably 900 to 1050 ° C, more preferably 900 to 1000 ° C, and still more preferably 910 to 970 ° C. Since the piezoelectric ceramic composition contained in the piezoelectric green sheet has the specific composition as described above, the firing temperature is capable of simultaneous firing of the internal electrode having a lower Ag ratio and a higher Ag ratio. Even so, it can be sufficiently sintered to obtain excellent piezoelectric characteristics (particularly high piezoelectric strain constant).

  Then, two end faces (end faces where the internal electrodes 1a and 1b are exposed) in the stacking direction in the fired laminate are subjected to a polishing treatment such as barrel polishing or sand blasting as necessary, and then the external electrode 4 Bake each. Specifically, an external electrode paste including a metal and an organic binder constituting the external electrode 4 is applied to the end face of the laminate, and then fired. In addition, you may form the external electrode 4 by methods, such as sputtering, vapor deposition, and electroless plating, besides baking. In this way, the multilayer piezoelectric element 10 having the structure shown in FIG. 1 is obtained.

  The piezoelectric ceramic composition, the piezoelectric ceramic, and the laminated piezoelectric element according to the preferred embodiments of the present invention have been described above, but the present invention is not necessarily limited to these embodiments, and does not depart from the spirit of the present invention. You may change suitably.

  EXAMPLES Hereinafter, although an Example demonstrates this invention still in detail, this invention is not limited to these Examples.

[Example A; Effect of Cu element]
(Example 1-1, Comparative Examples 1-1 to 1-10)
First, a starting material of a composite oxide represented by (Pb _1-β Me ¹ _β ) _α [(Me ² _1/3 Nb _2/3 ) _a Ti _b Zr _c ] O ₃ (1) as a main component is prepared. Got ready. That is, PbO powder, Me ¹ raw material powder, Me ² raw material powder, Nb ₂ O ₅ powder, TiO ₂ powder and ZrO ₂ powder are prepared as the main component raw materials, and these have the composition shown in Table 1 below. Weighed out. In Example A, raw material compositions for obtaining various piezoelectric ceramics shown in Table 1 were prepared using Sr as Me ¹ and each element shown in Table ² as Me ² . As raw materials for Me ¹ or Me ² elements, oxides of these elements were used.

  Next, each raw material composition was wet-mixed for 16 hours using a ball mill and then calcined at 700 to 900 ° C. for 2 hours in the air. The obtained calcined product was finely pulverized and then wet pulverized for 16 hours using a ball mill to obtain a calcined powder (piezoelectric ceramic composition). After drying this, an acrylic resin was added as a binder and granulated to obtain a disk-shaped molded body having a diameter of 17 mm and a thickness of 1 mm at a pressure of about 445 MPa using a uniaxial press molding machine.

  After molding, the resulting molded body was heat treated to remove the binder, and then subjected to heat treatment at 950 ° C. for 2 hours to form a piezoelectric ceramic. Then, an Ag paste containing Ag powder was printed on both surfaces of the obtained sintered body and baked at 350 ° C., and further an electric field of 3 kV was applied for 15 minutes in 120 ° C. silicone oil to perform polarization treatment. As a result, a sample for measuring the piezoelectric constant d33 obtained using each raw material composition was obtained.

  And about each sample produced in this way, the piezoelectric strain constant d33 was measured using d33 meter (Chinese Academy of Science voice research laboratory d33 meter; MODEL ZJ-3D). Table 1 shows the results obtained using each sample. In Table 1, “Evaluation NG” means that d33 could not be measured because the sintering was extremely bad.

From Table 1, when the piezoelectric ceramic containing Cu as the Me ² element is fired at 950 ° C., which can be fired simultaneously with the internal electrode made of Ag, a metal other than Cu (Zn, Mg, Fe, Sb) , Sn, Yb, In, Mn, Co, Cr), it was confirmed that the piezoelectric ceramic had a high piezoelectric strain constant as compared with the piezoelectric ceramic used.

[Example B: Evaluation of influence by composition of composite oxide]
(Examples 2-1 to 2-4, Comparative examples 1-1 to 2-2)
The composition of the composite oxide constituting the piezoelectric ceramic was changed as shown in Table 2, specifically, the same as in Example A, except that the ratio α of the A site element was changed variously. Samples for measuring various piezoelectric constants d33 were prepared, and d33 was measured in the same manner. The obtained results are shown in Table 2.

  From Table 2, the sample of the example in which the ratio α of the A site element of the composite oxide was within the scope of the present invention was fired at 950 ° C., which can be cofired with the internal electrode made of Ag. In this case, it was confirmed that a higher piezoelectric strain constant was obtained compared to the sample of the comparative example in which the ratio α was outside the range of the present invention.

(Examples 3-1 to 3-4, Comparative example 3-1)
The composition of the composite oxide constituting the piezoelectric ceramic was changed as shown in Table 3, specifically, various substitution amounts β of Me ¹ (Sr), which is a substitution element of Pb, which is an A-site element. Except for the change, various samples for measuring the piezoelectric constant d33 were prepared in the same manner as in Example A, and these d33 were measured in the same manner. The obtained results are shown in Table 3.

  From Table 3, the sample of the example in which the substitution amount β of Pb, which is an A site element, with Me element (Sr) was within the scope of the present invention was 950 ° C. capable of co-firing with an internal electrode made of Ag. It was confirmed that a higher piezoelectric strain constant can be obtained when the firing is carried out with the sample of the comparative example in which the substitution amount β is outside the range of the present invention.

(Examples 4-1 to 4-8, Comparative examples 4-1 to 4-4)
The composition of the complex oxide constituting the piezoelectric ceramic was changed as shown in Table 4, specifically, the ratio a of Cu and Nb as the B site element, the ratio b of Ti, and the ratio c of Zr. Various samples for measuring the piezoelectric constant d33 were prepared in the same manner as in Example A except that each was changed, and these d33 were measured in the same manner. Table 4 shows the obtained results.

  From Table 4, the sample of the example in which the ratio a of Cu and Nb as the B-site element, the ratio b of Ti, and the ratio c of Zr were within the scope of the present invention were co-fired with the internal electrode made of Ag. When firing at 950 ° C., which is possible, it was confirmed that a higher piezoelectric strain constant was obtained compared to the comparative sample in which these ratios were outside the scope of the present invention.

(Examples 5-1 to 5-3)
The composition of the complex oxide constituting the piezoelectric ceramic was changed as shown in Table 5, specifically, except that the Me ¹ element in the complex oxide was replaced with Sr instead of Ca or Sr. Samples for measuring various piezoelectric constants d33 were prepared in the same manner as in Example A, and these d33 were measured in the same manner. The results obtained are shown in Table 5.

  From Table 5, when Ca, Sr, and Ba are used as Me, which is the A site element of the composite oxide that is the main component, firing is performed at 950 ° C. that allows simultaneous firing with the internal electrode made of Ag. It was also confirmed that a sufficiently high piezoelectric strain constant was obtained.

It is a figure which shows typically the cross-sectional structure of the laminated piezoelectric element which concerns on suitable embodiment.

Explanation of symbols

  DESCRIPTION OF SYMBOLS 1a, 1b ... Internal electrode, 2 ... Piezoelectric layer, 3a, 3b ... Protective layer, 4 ... External electrode, 10 ... Multilayer type piezoelectric element.

Claims (2)

A piezoelectric ceramic comprising a composite oxide represented by the following composition formula (1) as a main component.
_{(Pb 1-β Me β)} α [(Cu 1/3 Nb 2/3) a Ti b Zr c] O 3 ... (1)
[In the formula (1), Me is at least one element selected from the group consisting of Ca, Sr and Ba, and α, β, a, b and c are the following formulas (2), (3 ), (4), (5), (6), and (7).
0.99 ≦ α ≦ 1.005 (2)
0 ≦ β ≦ 0.1 (3)
0.005 ≦ a ≦ 0.10 (4)
0.40 ≦ b ≦ 0.50 (5)
0.40 ≦ c ≦ 0.58 (6)
a + b + c = 1 (7)] A piezoelectric layer comprising the piezoelectric ceramic according to claim 1;
An electrode layer having an Ag content of 85% by mass or more;
A multilayer piezoelectric element comprising:

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