Patent Application
20160060158
The present application claims priority from Japanese Patent application serial No. 2014-175580, filed on Aug. 29, 2014, the content of which is hereby incorporated by reference into this application.
1. Field of the Invention
The present invention relates to lead-free low-melting glass compositions. Specifically, the present invention relates to a lead-free low-melting glass composition that is prevented or restrained from crystallization and can thereby soften and flow satisfactorily at a lower temperature. The present invention also relates to a low-temperature sealing glass frit, a low-temperature sealing glass paste, a conductive material, and a conductive glass paste, each of which contains the lead-free low-melting glass composition; and to a glass-sealed component and an electrical/electronic component prepared by using any of them.
2. Description of Related Art
In some articles, a low-temperature sealing glass frit including a low-melting glass composition and low-thermal-expansion ceramic particles is used typically for sealing and/or bonding. The articles are exemplified by vacuum-insulating double glass panels applied typically to window panes; display panels such as plasma display panels, organic electroluminescent display panels, and fluorescent display tubes; and electrical/electronic components such as quartz resonators, IC ceramic packages, and semiconductor sensors. The low-temperature sealing glass frit is often applied in the form of a low-temperature sealing glass paste. The low-temperature sealing glass paste is applied typically by a screen process printing or dispensing, dried, and fired for use in sealing and/or bonding. Upon the sealing and/or bonding, the low-melting glass composition contained in the low-temperature sealing glass frit or in the corresponding low-temperature sealing glass paste softens, flows, and thereby comes in intimate contact with a member to be sealed and/or to be bonded.
Likewise, a conductive material including a low-melting glass composition and metal particles is used to form an electrode and/or an interconnection in many electrical/electronic components such as solar cells, image display devices, multilayer capacitors, quartz resonators, LEDs (light-emitting diodes), and multilayered circuit boards. The conductive material is also used as a conductive bonding material for conduction. The conductive material is often applied in the form of a conductive glass paste, as with the low-temperature sealing glass frit. The conductive glass paste is applied typically by a screen process printing or dispensing, dried, and fired to form an electrode, an interconnection, and/or a conductive junction. Also upon the formation, the low-melting glass composition contained in the conductive material or in the corresponding conductive glass paste softens, flows, and thereby allows the metal particles to sinter or to be brought into intimate contact with a substrate.
The low-melting glass compositions to be contained in the low-temperature sealing glass frit or the corresponding low-temperature sealing glass paste, as well as the conductive material and the corresponding conductive glass paste have often employed PbO—B2O3 low-melting glass compositions containing a very large amount of lead oxide. The PbO—B2O3 low-melting glass compositions have a low softening point of 350° C. to 400° C., can soften and flow satisfactorily at 400° C. to 450° C., and still have relatively high chemical stability. The “softening point” refers to a second endothermic peak temperature as determined by a differential thermal analysis “DTA”.
However, more safe materials have been demanded in the electrical and electronic equipment industry in accordance with the recent global trend toward green procurement/green design. Typically, the Directive on the restriction of the use of certain hazardous substances in electrical and electronic equipment (RoHS directive) took effective on 1 Jul. 2006 by the European Union. The RoHS directive restricts the use of six hazardous materials, i.e., lead, mercury, cadmium, hexavalent chromium, polybrominated biphenyls, and polybrominated diphenyl ether.
The PbO—B2O3 low-melting glass compositions contain a large amount of lead that is restricted by the RoHS directive and are hardly applied to low-temperature sealing glass frits, corresponding low-temperature sealing glass pastes, conductive materials, and corresponding conductive pastes. Thereby, the development of novel lead-free low-melting glass compositions has proceeded. In addition, strong demands have been made to develop lead-free low-melting glass compositions that soften and flow at a lower temperature as compared with the PbO—B2O3 low-melting glass compositions and still have good chemical stability. These demands have been made so as to allow various glass-sealed components and electrical/electronic components to less undergo thermal damage (to have higher functions) and to have better productivity (with reduced takt time). Specifically, demands have been made to provide lead-free low-melting glass compositions that soften and flow at a temperature of 350° C. or lower, preferably 300° C. or lower, and are applicable typically to sealing and/or bonding or to the formation of electrodes/interconnections and conductive junctions.
Japanese Patent Application Laid-Open No. 2013-32255 (Patent Literature 1) discloses a lead-free low-melting glass composition. The glass composition contains, in terms of oxides, 10 to 60 mass percent of Ag2O, 5 to 65 mass percent of V2O5, and 15 to 50 mass percent of TeO2. The glass composition contains Ag2O, V2O5, and TeO2 in a total content of 75 mass percent to less than 100 mass percent, with the remainder being at least one of P2O5, BaO, K2O, WO3, Fe2O3, MnO2, Sb2O3, and ZnO in a content of greater than 0 mass percent to 25 mass percent.
The patent literature mentions that the Ag2O—V2O5—TeO2 lead-free low-melting glass composition has a low softening point of 320° C. or lower, softens and flows at a lower temperature as compared with the conventional PbO—B2O3 low-melting glass compositions, and still has good chemical stability, where the softening point is determined from the second endothermic peak temperature by the differential thermal analysis (DTA). In addition, Patent Literature 1 proposes a low-temperature sealing glass frit, a low-temperature sealing glass paste, a conductive material, and a conductive glass paste each containing the Ag2O—V2O5—TeO2 lead-free low-melting glass composition; and an electrical/electronic component prepared using any of them.
The present invention provides, in an embodiment, a lead-free low-melting glass composition containing a principal component; and an additional component, the principal component including a vanadium oxide, a tellurium oxide and a silver oxide, the additional component including at least one selected from the group consisting of yttrium oxide and lanthanoid oxides, in which a content of the additional component is 0.1 to 3.0 mole percent in terms of oxide.
The present invention allows a lead-free low-melting glass composition containing a vanadium oxide, a tellurium oxide, and a silver oxide to have a smaller crystallization tendency and to be prevented or restrained from crystallization upon heating-firing. This provides a lead-free low-melting glass composition that softens and flows more satisfactorily at a temperature of 350° C. or lower, and preferably 300° C. or lower, still has excellent chemical stability, and meets the RoHS directive.
The lead-free low-melting glass composition according to the embodiment of the present invention, when combined with ceramic particles and/or metal particles, can give a low-temperature sealing glass frit, a low-temperature sealing glass paste, a conductive material, and a conductive glass paste each of which can enjoy advantageous effects of the lead-free low-melting glass composition according to the embodiment of the present invention.
The low-temperature sealing glass frit, low-temperature sealing glass paste, conductive material, and conductive paste each containing the lead-free low-melting glass composition according to the embodiment of the present invention, when applied, can give a glass-sealed component and an electrical/electronic component that includes an electrode/interconnection or a conductive junction. The glass-sealed component, the electrode/interconnection, and the conductive junction are sealed, bonded, or formed at a firing temperature of 350° C. or lower, and preferably 300° C. or lower. These components are obtained after consideration of influence on the environmentalburden. Specifically,useofthelead-freelow-melting glass composition according to the embodiment of the present invention allows the glass-sealed component and the electrical/electronic component to less undergo thermal damage (to have higher functions), to have better productivity (to require reduced takt time) and better reliability (chemical stability at certain level), and to put less burden on the environment.
The Ag2O—V2O5—TeO2 lead-free low-melting glass composition disclosed in Patent Literature 1 certainly has a lower softening point as compared with the conventional PbO—B2O3 low-melting glass compositions, but has a tendency to crystallize and thereby softens and flows unsatisfactorily due to the crystallization tendency upon heating-firing. Specifically, with insufficient consideration on the crystallization tendency, the glass composition disadvantageously softens and flows unsatisfactorily at a low temperature of 350° C. or lower, and preferably 300° C. or lower. Assume that the glass composition is mixedwith low-thermal-expansion ceramic particles or metal particles or is formed into a paste upon usage. In this case, the glass composition more significantly undergoes crystallization. This causes the glass composition to be hardly expanded into low-temperature sealing glass frits, low-temperature sealing glass pastes, conductive materials, and conductive pastes and to be hardly applied to glass-sealed components and electrical/electronic components obtained using any of them.
It is an object of the present invention to prevent or restrain the crystallization of a Ag2O—V2O5—TeO2 lead-free low-melting glass composition and to thereby provide a lead-free low-melting glass composition that satisfactorily softens and flows at a temperature of 350° C. or lower, and preferably 300° C. or lower. It is another object of the present invention to provide, based on the above, a lead-free low-melting glass composition that has a smaller crystallization tendency even when mixed with low-thermal-expansion ceramic particles or metal particles, or formed into a paste. It is yet another object of the present invention to expand the lead-free low-melting glass composition so as to provide a low-temperature sealing glass frit, a low-temperature sealing glass paste, a conductive material, and a conductive glass paste; and a glass-sealed component and an electrical/electronic component obtained using any of them.
The present invention provides a lead-free low-melting glass composition that contains a vanadium oxide, a tellurium oxide, and a silver oxide and further contains an additional component including at least one selected from yttrium oxide and lanthanoid oxides. The lead-free low-melting glass composition contains the additional component in a content in terms of oxide of 0.1 to 3.0 mole percent. As used herein the term “lead-free” also refers to and includes one containing the restricted materials in contents at the restricted levels or lower as restricted in the RoHS directive (that took effective on 1 Jul. 2006). The restricted level is 1000 ppm or less for lead (Pb).
The glass composition may contain, as the additional component, at least one selected from the group consisting of Y2O3, La2O3, CeO2, Er2O3, and Yb2O3 in a content (total content) in terms of oxide of 0.1 to 2.0 mole percent. In particular, the glass composition may effectively contain at least one of Y2O3 and La2O3 as the additional component. The glass composition more preferably contains the additional component in the content of 0.1 to 1.0 mole percent.
The lead-free low-melting glass composition according to the embodiment of the present invention preferably contains V2O5, TeO2, and Ag2O in a total content in terms of oxide of 85 mole percent or more and preferably has contents of TeO2 and Ag2O each 1 to 2 times as much as the content of V2O5. The glass composition preferably further contains at least one of BaO, WO3, and P2O5 in a content (total content) in terms of oxide of 13 mole percent or less.
The lead-free low-melting glass composition according to the embodiment of the present invention may have a softening point of 280° C. or lower, where the softening point is determined by a differential thermal analysis (DTA) as a second endothermic peak temperature. The glass composition may have a crystallization onset temperature higher than the second endothermic peak temperature (softening point) by 60° C. or more, where the crystallization onset temperature is determined by the differential thermal analysis (DTA).
The present invention provides, in another embodiment, a low-temperature sealing glass frit containing 40 to 100 volume percent of the lead-free low-melting glass composition and 0 to 60 volume percent of low-thermal-expansion ceramic particles. Herein, the low-temperature sealing glass frit contains the lead-free low-melting glass composition and the low-thermal-expansion ceramic particles.
Hence, the content of the lead-free low-melting glass composition is actually less than 100 volume percent, and the content of the low-thermal-expansion ceramic particles is actuallymore than 0 volume percent. The same applies in the following numerical ranges.
The low-thermal-expansion ceramic particles preferably include at least one selected from the group consisting of zirconium phosphate tungstate (Zr2 (WO4) (PO4)2), quartz glass (SiO2), zirconium silicate (ZrSiO4), aluminum oxide (Al2O3), mullite (3Al2O3.2SiO2), and niobium oxide (Nb2O5). In particular, the low-thermal-expansion ceramic particles are preferably particles of zirconium phosphate tungstate (Zr2(WO4) (PO4)2) and/or particles of a compound containing mainly zirconium phosphate tungstate (Zr2(WO4) (PO4)2). The glass frit effectively contains 30 to 50 volume percent of the low-thermal-expansion ceramic particles.
The low-temperature sealing glass frit may be prepared from a low-temperature sealing glass paste that contains the lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, low-thermal-expansion ceramic particles, and a solvent. In the low-temperature sealing glass paste, the low-thermal-expansion ceramic particles preferably include at least one selected from the group consisting of zirconium phosphate tungstate (Zr2(WO4)(PO4)2), quartz glass (SiO2), zirconium silicate (ZrSiO4), aluminum oxide (Al2O3), mullite (3Al2O3.2SiO2), and niobium oxide (Nb2O5), and the solvent preferably includes α-terpineol and/or diethylene glycol n-butyl ether acetate (e.g., Butyl CARBITOL Acetate). In particular, the low-thermal-expansion ceramic particles effectively include zirconium phosphate tungstate (Zr2(WO4) (PO4)2) and/or a compound containing mainly zirconium phosphate tungstate (Zr2(WO4) (PO4)2), and the solvent effectively includes α-terpineol.
The present invention provides, in yet another embodiment, a conductive material containing 5 to 100 volume percent of the lead-free low-melting glass composition, and 0 to 95 volume percent of metal particles. The conductive material preferably contains, as the metal particles, at least one selected from the group consisting of silver (Ag), silver alloys, copper (Cu), copper alloys, aluminum (Al), aluminum alloys, tin (Sn), and tin alloys. In particular, the conductive material preferably contains at least one of silver (Ag) and aluminum (Al) as the metal particles. The content of the metal particles is effectively 10 to 90 volume percent.
The conductive material may be formed from a conductive glass paste that contains the lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, and a solvent. The conductive glass paste may further contain metal particles. The metal particles may include at least one selected from the group consisting of silver (Ag), silver alloys, copper (Cu), copper alloys, aluminum (Al), aluminum alloys, tin (Sn), and tin alloys. The solvent preferably includes α-terpineol and/or diethylene glycol n-butyl ether acetate. In an effective embodiment, the metal particles may include silver (Ag) and/or aluminum (Al), and the solvent may include α-terpineol.
The present invention provides, in still another embodiment, a glass-sealed component including a seal portion containing a lead-free low-melting glass phase. The seal portion contains 40 to 100 volume percent of the lead-free low-melting glass phase. The lead-free low-melting glass phase may be derived from the lead-free low-melting glass composition according to the embodiment of the present invention. The glass-sealed component can be effectively expanded typically into vacuum-insulating double glass panels and display panels.
The present invention provides, in another embodiment, an electrical/electronic component including at least one unit selected from electrodes, interconnections, and conductive junctions, where the at least one unit contains the lead-free low-melting glass phase. The unit contains 5 to 100 volume percent of the lead-free low-melting glass phase and 0 to 95 volume percent of metal particles. The electrical/electronic component can be effectively expanded typically into solar cells, image display devices, multilayer capacitors, quartz resonators, LEDs (light-emitting diodes), and multilayered circuit boards.
The present invention will be illustrated in further detail with reference to certain embodiments thereof and the attached drawings. It should be noted, however, that the embodiments are never construed to limit the scope of the present invention; and that various combinations, changes, modifications, and improvements are possible without deviating from the spirit and scope of the present invention.
(Glass Composition)
In general, a low-melting glass composition more satisfactorily softens and flows at a low temperature with a decreasing characteristic temperature (e.g., glass transition point, yield point, or softening point). In contrast, the low-melting glass composition has a higher crystallization tendency, becomes more susceptible to crystallization upon heating-firing, and, contrarily, softens and flows unsatisfactorily at a low temperature with an excessively low characteristic temperature. In addition, a glass having a lower characteristic temperature has inferior chemical stability such as water resistance and acid resistance. This glass also has a tendency to put a larger burden on the environment. Typically, with an increasing content of hazardous PbO, the conventional PbO—B2O3 low-melting glass compositions can have lower characteristic temperatures, but have a higher crystallization tendency and lower chemical stability, and put larger burden on the environment.
The present inventors made intensive investigations on a glass composition that is a low-melting glass composition containing approximately no lead, but can soften and flow satisfactorily at a lower temperature as compared with the conventional PbO—B2O3 low-melting glass compositions, and still has good chemical stability. As a result, the present inventors have found that a novel low-melting glass composition meets the requirements simultaneously. The present invention has been made based on these findings.
As described above, the lead-free low-melting glass composition according to the embodiment of the present invention is a lead-free low-melting glass composition that contains a vanadium oxide, a tellurium oxide, and a silver oxide as principal components, and further contains 0.1 to 3.0 mole percent of an additional component including at least one selected from yttrium oxide and lanthanoid oxides. The present inventors have found that the lead-free low-melting glass composition can have a smaller crystallization tendency, when combined with a small amount of at least one selected from yttrium oxide and lanthanoid oxides. The glass composition effectively contains the additional component in the content within the range of 0.1 to 3.0 mole percent . The glass composition may hardly effectively have a smaller crystallization tendency, if containing the additional component in the content less than 0.1 mole percent. In contrast, the glass composition may suffer from higher characteristic temperatures such as softening point, or may have a higher crystallization tendency contrarily, if containing the additional component in the content greater than 3.0 mole percent. Of the yttrium oxide and lanthanoid oxides, Y2O3, La2O3, CeO2, Er2O3, and Yb2O3 are more effective for the reduction of crystallization tendency. The glass composition may effectively contain at least one of these oxides in the content of 0.1 to 2.0 mole percent. Among them, the glass composition may particularly effectively contain at least one of Y2O3 and La2O3 in the content of 0.1 to 1.0 mole percent.
Next, it will be illustrated how the vanadium oxide, tellurium oxide and silver oxide which are the principal components act in the lead-free low-melting glass composition. The silver oxide is contained so as to allow the glass composition to have lower characteristic temperatures such as glass transition point, yield point, and softening point and to have better chemical stability. The vanadium oxide is contained so as to prevent the silver oxide from reduction and from precipitating as metal silver upon glass production. The silver oxide contained as a glass component may fail to effectively offer characteristic temperatures at desired low levels unless it is present in the form of silver ion in the glass. The glass composition can offer lower characteristic temperatures with an increasing content of the silver oxide, i.e., with an increasing amount of silver ions in the glass. However, this requires a higher content of the vanadium oxide so as to prevent or restrain the precipitation of metal silver. The glass can contain a monovalent silver ion in a number of up to 2 per one pentavalent vanadium ion upon its production. The tellurium oxide acts as a vitrification component so as to cause vitrification upon glass production. The glass composition fails to form glass, if containing no tellurium oxide. However, the tetravalent tellurium ion can effectively act when contained in a number up to 1 per one pentavalent vanadium ion. If the number is greater than 1, a compound between tellurium and silver may precipitate.
In consideration of the above-described functions and actions of the vanadium oxide, tellurium oxide, and silver oxide, the lead-free low-melting glass composition according to the embodiment of the present invention preferably has such a basic formulation that the total content of V2O5, TeO2, and Ag2O in terms of oxide is 85 mole percent or more, and the contents of TeO2 and Ag2O are each 1 to 2 times as much as the content of V2O5. Disadvantageously, if the glass composition has a basic formulation lower than or higher than the range, the glass composition may cause a metal silver precipitation upon glass production, may have less effectively lowered characteristic temperatures, may undergo a significant crystallization upon heating-firing, or may have an inferior chemical stability. In addition, the glass composition may further contain a secondary component including at least one of BaO, WO3, and P2O5 in the content in terms of the oxides of 13 mole percent or less. This is effective for the lead-free low-melting glass composition according to the embodiment of the present invention to form glass in a homogeneous vitreous state (amorphous state) and for the resulting glass to have a smaller crystallization tendency. However, the glass composition may have higher characteristic temperatures, if containing the secondary component in the content greater than 13 mole percent.
As having the above-mentioned configuration, the lead-free low-melting glass composition according to the embodiment of the present invention can have a softening point of 280° C. or lower, where the softening point is determined by the differential thermal analysis (DTA) as a second endothermic peak temperature. In addition, the glass composition can have a crystallization onset temperature higher than the second endothermic peak temperature (softening point) by 60° C. or more, where the crystallization onset temperature is determined by the DTA. The lead-free low-melting glass composition according to the embodiment of the present invention preferably has a lower softening point and, in contrast, a higher crystallization onset temperature. This allows the glass composition to soften and flow at a low temperature more satisfactorily. This is preferred so as to expand the glass composition into low-temperature sealing glass frits, low-temperature sealing glass pastes, conductive materials, and conductive pastes and to apply them to glass-sealed components and electrical/electronic components. However, conventional low-melting glass compositions may often suffer from a lower crystallization onset temperature, when designed to have a lower softening point.
The characteristic temperatures in the present invention will be described below. The characteristic temperatures herein are measured by the differential thermal analysis (DTA).
Assume that a low-melting glass composition is used to seal and/or bond various parts or components or to form electrodes/interconnections and conductive junctions. In this process, the low-melting glass composition is fired generally frequently at a preset temperature higher than the softening point Ts by about 20° C. to about 60° C., although the firing temperature may vary depending typically on the type, content, and particle diameter of the contained low-thermal-expansion ceramic particles or metal particles, and on the firing conditions such as rate of temperature rise, atmosphere, and pressure. The low-melting glass composition has to satisfactorily soften and flow at that firing temperature. It is therefore very important to minimize the crystallization of the low-melting glass composition at the firing temperature.
(Low-Temperature Sealing Glass Frit and Low-Temperature Sealing Glass Paste)
The low-temperature sealing glass frit according to an embodiment of the present invention contains 40 to 100 volume percent of the lead-free low-melting glass composition according to the embodiment of the present invention, and 0 to 60 volume percent of low-thermal-expansion ceramic particles. The low-temperature sealing glass paste according to an embodiment of the present invention contains the lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, low-thermal-expansion ceramic particles, and a solvent. The glass frit may fail to achieve good sealing and/or bonding, if containing the lead-free low-melting glass composition according to the embodiment of the present invention in the content less than 40 volume percent, or if containing the low-thermal-expansion ceramic particles in the content greater than 60 volume percent.
Some low-thermal-expansion ceramic particles allow the lead-free low-melting glass composition according to the embodiment of the present invention to less undergo crystallization. The glass frit or glass paste may preferably contain, as such low-thermal-expansion ceramic particles, at least one selected from the group consisting of zirconium phosphate tungstate (Zr2(WO4) (PO4)2) quartz glass (SiO2), zirconium silicate (ZrSiO4), aluminum oxide (Al2O3), mullite (3Al2O3.2SiO2), andniobium oxide (Nb2O5). Among these low-thermal-expansion ceramic particles, zirconium phosphate tungstate (Zr2(WO4) (PO4)2) and/or a compound containing mainly zirconium phosphate tungstate (Zr2(WO4) (PO4)2) is effective to allow the low-temperature sealing glass frit according to the embodiment of the present invention to less undergo thermal expansion. The glass frit preferably contains at least one of the components in a content of 30 to 50 volume percent. Some solvents allow the lead-free low-melting glass composition according to the embodiment of the present invention to less undergo crystallization. Such solvents are exemplified by α-terpineol and diethylene glycol n-butyl ether acetate, of which α-terpineol is particularly effective. The low-temperature sealing glass paste may further contain one or more additives such as viscosity modifier and wetting agents as needed so as to control the stability and coatability.
Assume that the low-temperature sealing glass frit or low-temperature sealing glass paste according to the embodiment of the present invention is used for sealing and/or bonding to form a glass-sealed component. In this case, the low-temperature sealing glass frit or low-temperature sealing glass paste is arranged in or applied to a portion of an article to be sealed or to be bonded, and is fired at a temperature higher than the softening point Ts of the contained lead-free low-melting glass composition by about 20° C. to about 60° C. The low-temperature sealing glass frit and low-temperature sealing glass paste according to the embodiments of the present invention each contain the lead-free low-melting glass composition having a lower softening point and having a smaller crystallization tendency, can thereby soften and flow more satisfactorily at a low temperature, and can be fired at a lower temperature. This reduces the burden on the environment and still allows the glass-sealed component to less undergo thermal damage (to have higher functions) and to offer better productivity (with reduced takt time). In addition, the lead-free low-melting glass composition according to the embodiment of the present invention has good chemical stability. This allows the glass-sealed component to have reliability at certain level.
(Conductive Material and Conductive Glass Paste)
The conductive material according to an embodiment of the present invention contains 5 to 100 volume percent of the lead-free low-melting glass composition according to the embodiment of the present invention, and 0 to 95 volume percent of metal particles. The conductive glass paste according to the embodiment of the present invention contains the lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, metal particles, and a solvent. The conductive material, if containing the lead-free low-melting glass composition according to the embodiment of the present invention in a content less than 5 volume percent, or if containing the metal particles in a content greater than 95 volume percent, may cause insufficient sintering between the metal particles or may offer insufficient bonding (adhesion) to a substrate.
Some metal particles offer good conductivity when mixed with the lead-free low-melting glass composition according to the embodiment of the present invention. Such metal particles may include at least one selected from the group consisting of silver (Ag), silver alloys, copper (Cu), copper alloys, aluminum (Al), aluminum alloys, tin (Sn), and tin alloys . Of these metal particles, silver (Ag) and/or aluminum (Al) particles are effective for allowing the conductive material according to the embodiment of the present invention to have a lower electric resistance. The conductive material may contain at least one of silver (Ag) and aluminum (Al) preferably in the content of 10 to 90 volume percent. This is because the lead-free low-melting glass composition according to the embodiment of the present invention can accelerate the sintering of silver (Ag) particles and can remove the surface oxide film of aluminum (Al) particles. Alpha-terpineol and diethylene glycol n-butyl ether acetate (e.g., Butyl CARBITOL Acetate) are preferred as the solvent for the lead-free low-melting glass composition according to the embodiment of the present invention, of which α-terpineol is particularly effective, as with the low-temperature sealing glass paste according to the embodiment of the present invention. The conductive glass paste may further contain one or more additives such as viscosity modifiers and wetting agents as needed so as to control the stability and coatability.
Assume that the conductive material or conductive glass paste according to the embodiment of the present invention is used so as to form an electrode/interconnection and/or a conductive junction in an electrical/electronic component. In this case, the conductive material or conductive glass paste may be arranged in or applied to a predetermined portion typically of a substrate, and is fired at a temperature higher than the softening point Ts of the contained lead-free low-melting glass composition by about 20° C. to about 60° C. Assume that the metal particles to be used include a metal that is susceptible to oxidation. In this case, the firing is preferably performed in an inert gas atmosphere or in a vacuum atmosphere so as to prevent the metal particles from oxidation.
The conductive material and conductive glass paste according to embodiments of the present invention contain the lead-free low-melting glass composition having a lower softening point and a smaller crystallization tendency, can thereby soften and flow more satisfactorily at a low temperature, and can be fired at a lower temperature. Specifically, the conductive material and conductive glass paste can form the electrode/interconnection and/or the conductive junction at a lower temperature, namely, can be fired at a lower temperature. This reduces the burden on the environment and still allows the electrical/electronic component to undergo less thermal damage (to have higher functions) and to offer better productivity (with reduced takt time). In addition, the lead-free low-melting glass composition according to the embodiment of the present invention has good chemical stability. This allows the electrical/electronic component to have reliability at a certain level.
(Glass-Sealed Component)
The glass-sealed component according to an embodiment of the present invention is not limited, as long as including a portion sealed and/or bonded with any of the low-temperature sealing glass frit and low-temperature sealing glass paste according to the embodiments of the present invention. Preferred examples of the glass-sealed component include vacuum-insulating double glass panels applied typically to window panes; as well as display panels such as plasma display panels, organic electroluminescent display panels, and fluorescent display tubes. The glass frit and glass paste can also be expanded typically into bonding in electrical/electronic components such as quartz resonators, IC ceramic packages, and semiconductor sensors.
(Electrical/Electronic Component)
The electrical/electronic component according to an embodiment of the present invention is not limited, as long as including an electrode/interconnection and/or a conductive junction formed using any of the conductive material and conductive glass paste according to embodiments of the present invention. Preferred examples of the electrical/electronic component include solar cells, image display devices, multilayer capacitors, quartz resonators, LEDs, and multilayered circuit boards.
The present invention will be illustrated in further detail with reference to specific experimental examples. It shouldbe noted, however, that the experimental examples are never construed to limit the scope of the present invention; and that various modifications and variations are possible without deviating from the spirit and scope of the present invention.
In this experimental example, a trace amount of any of yttrium oxide and lanthanoid oxides was added as an additional component to a lead-free low-melting glass composition containing a vanadium oxide, a tellurium oxide, and a silver oxide as principal components. In this process, how the addition affects the glass properties was examined. The lead-free low-melting glass composition basically contains 21V2O5-38TeO2-37Ag2O-3BaO-1WO3 (mole percent) as a formulation upon glass production. The yttrium oxide used herein was Y2O3, and the lanthanoid oxides were La2O3, CeO2, Pr2O3, Nd2O3, Sm2O3, Gd2O3, Dy2O3, Er2O3, and Yb2O3. The lead-free low-melting glass composition contained any one of these oxides in a content of 0.3 mole percent. The additional component was added while replacing part of WO3 . Namely, the WO3 content herein was set to 0 .7 mole percent.
In this experimental example, eleven different lead-free low-melting glass compositions VTA-00 to VTA-10 including one having the basic formulation were prepared. The resulting lead-free low-melting glass compositions were examined and evaluated on vitrification, characteristic temperatures in relation to crystallization tendency, and chemical stability. VTA-00 had the basic glass formulation of 21V2O5-38TeO2-37Ag2O-3BaO-1WO3 (mole percent). VTA-01 to VTA-10 are glass compositions containing WO3 in the content of 0.7 mole percent and respectively containing Y2O3, La2O3, CeO2, Pr2O3, Nd2O3, Sm2O3, Gd2O3, Dy2O3, Er2O3, and Yb2O3 in the content of 0.3 mole percent.
(Preparation of Lead-Free Low-Melting Glass Composition)
Lead-free low-melting glass compositions VTA-00 to VTA-10 as in Table 1 were prepared. The formulations given in Table 1 are formulations upon glass production. Starting materials used herein were powders of V2O5 (Shinko Chemical Co . , Ltd.), TeO2 (Kojundo Chemical Laboratory Co., Ltd.), Ag2O (Wako Pure Chemical Industries, Ltd.), BaCO3 (Kojundo Chemical Laboratory Co., Ltd.), and WO3 (Kojundo Chemical Laboratory Co., Ltd.). The yttrium oxide and lanthanoid oxides used herein were powders of Y2O3, La2O3, CeO02, Pr2O3, Nd2O3, Sm2O3, Gd2O3, Dy2O3, Er2O3, and Yb2O3 each supplied by Kojundo Chemical Laboratory Co., Ltd.
Individual starting material powders were weighed, formulated, and mixed to a total amount of about 200 g, and the mixture was placed in a quartz glass crucible. The quartz glass crucible housing the starting material powder mixture was placed in a glass melter, heated to a temperature of 700° C. to 750° C. at a rate of temperature rise of about 10° C. per minute, and held at the temperature for one hour with stirring using an aluminum oxide rod so as to uniformize the formulation of the melt in the quartz glass crucible. The quartz glass crucible was retrieved from the glass melter, the melt was poured into a stainless steel mold previously heated to about 120° C., and thereby yielded the lead-free low-melting glass compositions VTA-00 to VTA-10. Next, each of the prepared lead-free low-melting glass compositions was pulverized to a size of about 10 μm.
1)21V2O5—38TeO2—38Ag2O—3BaO—1WO3 (mole percent)
2)21V2O5—38TeO2—38Ag2O—3BaO—0.7WO3—0.3 additional component (mole percent)
3)84PbO—13B2O3—2SiO2—1Al2O3 (mass percent)
(Evaluation of Vitrification)
The prepared lead-free low-melting glass compositions VTA-00 to VTA-10 were subjected to X-ray diffractometry to determine whether crystallization occurred in each glass composition in the form of powder and to evaluate the vitrification. A sample suffering from no crystallization was considered to be vitrified satisfactorily and evaluated as “accepted”. In contrast, a sample suffering from crystallization was considered to fail to have a homogeneous amorphous state as a result of vitrification and evaluated as “rejected”.
(Evaluation of Characteristic Temperatures and Crystallization Tendency)
The prepared lead-free low-melting glass compositions VTA-00 to VTA-10 were subjected to differential thermal analysis (DTA) using a powder of each glass composition to evaluate or determine their characteristic temperatures and crystallization tendency. The DTA was performed with a macrocell system, where about 500 mg of a sample glass powder was placed in the macrocell, heated in the air from room temperature up to 400° C. at a rate of temperature rise of 5° C. per minute to plot a DTA curve as illustrated in
(Evaluation of Chemical Stability)
The prepared lead-free low-melting glass compositions VTA-00 to VTA-10 were each subjected to a water resistance test and an acid resistance test to evaluate a chemical stability. Glass test specimens were cullet having a size of about 10 to about 20 mm before pulverization. In the water resistance test, the cullet was immersed in pure water at 50° C. for 48 hours. In the acid resistance test, the cullet was immersed in a 1 N aqueous nitric acid solution at room temperature for 24 hours. The cullet specimens after the two tests were visually observed on appearance. A sample offering no change in appearance was evaluated as “accepted”, whereas a sample offering a change in appearance was evaluated as “rejected”. As a comparative example, cullet of conventional lead-containing low-melting glass composition PB-1 was subjected to the tests as above. The lead-containing low-melting glass composition used as a comparative example had a formulation of 84PbO-13B2O3-2SiO2-1Al2O3 (mass percent), a glass transition point Tg of 313° C., a yield point Mg of 332° C., and a softening point Ts of 386° C.
Table 1 shows the evaluation results of the vitrification, characteristic temperatures in relation to crystallization tendency, and chemical stability of the lead-free low-melting glass compositions VTA-00 to VTA-10. Table 1 also shows the evaluation results of the conventional lead-containing low-melting glass composition PB-01.
The lead-free low-melting glass composition VTA-00 (comparative example) having the basic formulation had significantly low characteristic temperatures Tg, Mg, and Ts and can soften and flow at a significantly low temperature as compared with the lead-containing low-melting glass composition PB-01 (comparative example). The sample VTA-00 had very high chemical stability in spite of having low characteristic temperatures. The sample, however, had a crystallization tendency at a temperature around 260° C. The sample had a difference between the temperatures Tory and Ts of about 40° C., but offered a relatively large amount of heat liberated by crystallization, and could less satisfactorily soften and flow upon heating-firing. It was difficult to expand the sample into the sealing and/or bonding and into the formation of electrodes/interconnections and conductive junctions. In contrast, the lead-free low-melting glass compositions VTA-01 to VTA-10 (examples) containing a trace amount of one of yttrium oxide and lanthanoid oxides had a still lower crystallization tendency as compared with the comparative example VTA-00. In addition, the examples VTA-01 to VTA-10 had little rise in the characteristic temperatures Tg, Mg, and Ts and suffered from approximately no deterioration in chemical stability. For lanthanoid oxides, not all the lanthanoid elements of the periodic table were investigated herein. The lanthanoid elements, however, are known to have similar properties to each other due to their electronic states . Obviously, all the lanthanoid oxides can offer effects as mentioned above.
In particular, the data of VTA-01 to VTA-03, VTA-09, and VTA-10 demonstrated that the presence of at least one of Y2O3, La2O3, CeO2, Er2O3, and Yb2O3 significantly effectively contributes to a lower crystallization tendency. The data also demonstrated that, of the lanthanoid elements in lanthanoid oxides, those positioned at both ends of the range of atomic numbers (57 to 71) in the periodic table more effectively offer a lower crystallization tendency as compared with lanthanoid elements positioned in the center part in the range. The presence of Y2O3 and La2O3 most effectively contributes to a lower crystallization tendency. The samples VTA-01 andVTA-02 respectively containing Y2O3 and La2O3 could have such a significantly low crystallization tendency as to offer no exothermic crystallization peak.
These data and considerations demonstrated as follows. Assume that lead-free low-melting glass compositions contain a vanadium oxide, a tellurium oxide, and a silver oxide as principal components. These lead-free low-melting glass compositions, when further containing at least one of yttrium oxide and lanthanoid oxides as an additional component, can particularly have a lower crystallization tendency without significant rise in the softening point Ts and without deterioration in chemical stability. In particular, the presence of any of Y2O3, La2O3, CeO2, Er2O3 and Yb2O3 effectively offer a lower crystallization tendency, of which the presence of Y2O3 and/or La2O3 is most effective.
In this experimental example, lead-free low-melting glass compositions containing a vanadium oxide, a tellurium oxide, and a silver oxide as principal components and further containing any of yttrium oxide and lanthanoid oxides were prepared. How the content of any of the yttrium oxide and lanthanoid oxides affects the vitrification, characteristic temperatures in relation to crystallization tendency, and chemical stability was investigated. The yttrium oxide used herein was Y2O3, and the lanthanoid oxides used herein were La2O3, CeO2, and Er2O3, each of which was contained in a content of 0 to 5 mole percent.
The investigated formulations (mole percent) of the lead-free low-melting glass compositions are given in Table 2. The lead-free low-melting glass compositions were examined to evaluate the vitrification, characteristic temperatures in relation to crystallization tendency, and chemical stability, and the results are given in Table 3. The lead-free low-melting glass compositions were prepared and evaluated by the procedure of Experimental Example 1. VTA-11, VTA-26, VTA-27, VTA-45, VTA-46, and VTA-56 in Tables 2 and 3 are lead-free low-melting glass compositions containing none of yttrium oxide and lanthanoid oxides and were used as comparative examples. Other samples are lead-free low-melting glass compositions containing Y2O3 (VTA-12 to VTA-25), La2O3 (VTA-28 to VTA-44), CeO2 (VTA-47 to VTA-55), or Er2O3 (VTA-57 to VTA-63).
VTA-12 to VTA-25 were compared with VTA-11. The comparison demonstrated that VTA-12 to VTA-24 containing yttrium oxide Y2O3 in a content of 0.1 to 3.0 mole percent hada lower crystallization tendency. VTA-21 andVTA-23 further contained a lanthanoid oxide La2O3 in addition to Y2O3. VTA-13, VTA-15 to VTA-18, and VTA-20 contained at least one secondary component selected from BaO, WO3, and P2O5. The presence of at least one selected from BaO, WO3, and P2O5 in addition to Y2O3 (and further La2O3) had a still lower crystallization tendency. VTA-25 containing 5 mole percent of Y2O3 had a lower amount of heat liberated by crystallization about one third that of VTA-11, but had a lower crystallization onset temperature Tory. Of VTA-12 to VTA-24, VTA-12 to VTA-23 particularly effectively had a lower crystallization tendency and had a total content of Y2O3 and La2O3 of 0.1 to 2.0 mole percent. VTA-12 to VTA-25 had chemical stability without deterioration as compared with VTA-11 and each had a glass softening point Ts of 280° C. or lower. The softening point Ts, crystallization onset temperature Tory, and amount of heat liberated by crystallization of these samples were synthetically evaluated. This demonstrated that glass composition having a total content of Y2O3 and La2O3 of 0.1 to 1.0 mole percent are most effective, as indicated in data of VTA-12 to VTA-21.
VTA-28 to VTA-44 were compared with VTA-26 and VTA-27. The comparison demonstrated that VTA-28 to VTA-43 containing 0.1 to 3.0 mole percent of lanthanoid oxide La2O3 had a lower crystallization tendency. VTA-39, VTA-40, and VTA-42 further contained yttrium oxide Y2O3 in addition to La2O3. In particular, VTA-29 to VTA-40 could have such a significantly lower crystallization tendency as to offer no exothermic crystallization peak. This is because these samples contained at least one of BaO, WO3, and P2O5 in addition to La2O3 (and further Y2O3) as demonstrated by a comparison of VTA-26 and VTA-27 withVTA-11. As compared withVTA-27, VTA-44 containing 5 mole percent of La2O3 could have an amount of heat liberated by crystallization as reduced to the half, but had a somewhat lower crystallization onset temperature Tory. Of VTA-28 to VTA-43, VTA-28 to VTA-42 having a total content of La2O3 and Y2O3 of 0.1 to 2.0 mole percent had a particularly effectively lowered crystallization tendency. As compared with VTA-26 and VTA-27, VTA-28 to VTA-44 offered no deterioration in chemical stability and each had a glass softening point Ts of 280° C. or lower. The softening point Ts, crystallization onset temperature Tory, and amount of heat liberated by crystallization of the samples were synthetically evaluated. This demonstrated that glass compositions having a total content of La2O3 and Y2O3 of 0.1 to 1.0 mole percent are most effective as indicated in data of VTA-28 to VTA40.
VTA-47 to VTA-55 were compared with VTA-45 and VTA-46. This demonstrated that VTA-47 to VTA-54 containing 0.1 to 3.0 mole percent of a lanthanoid oxide CeO2 could have a lower crystallization tendency. VTA-47 to VTA-54 further contained a secondary component selected from BaO, WO3, and P2O5 in addition to CeO2. VTA-52 further contained Y2O3 and La2O3 in addition to CeO2. VTA-52 could have such a significantly lower crystallization tendency as to offer no exothermic crystallization peak as compared with VTA-50 containing CeO2 alone as the additional component. As compared with VTA-45, VTA-55 containing 5 mole percent of CeO2 could have an amount of heat liberated by crystallization as reduced to the half, but had a somewhat lower crystallization onset temperature Tcry. Of VTA-47 to VTA-54, VTA-47 to VTA-53 having a total content of CeO2, Y2O3, and La2O3 of 0.1 to 2.0 mole percent could effectively have a lower crystallization tendency. As comparedwithVTA-45 andVTA-46, VTA-47 toVTA-55 offered no deterioration in chemical stability and had a glass softening point Ts of 280° C. or lower. The softening point Ts, crystallization onset temperature Tcry, and amount of heat liberated by crystallization of the samples were synthetically evaluated. This demonstrated that glass compositions having a total content of CeO2, Y2O3, and La2O3 of 0.1 to 1.0 mole percent were most effective, as indicated in data of VTA-47 to VTA-52.
Of VTA-56 to VTA-63, VTA-57 to VTA-62 containing 0.1 to 3.0 mole percent of a lanthanoid oxide Er2O3 could have a lower crystallization tendency as compared with VTA-56. VTA-57 to VTA-62 further contained BaO and P2O5 as secondary components in addition to Er2O3. VTA-59 further contained another lanthanoid oxide La2O3 in addition to Er2O3. In particular, VTA-58 to VTA-60 could have such a significantly lower crystallization tendency as to offer no exothermic crystallization peak. This is because the samples contained BaO and P2O5 as secondary components in addition to Er2O3 (and further La2O3) as demonstrated by the comparison between VTA-56 and VTA-11. VTA-63 containing 5 mole percent of Er2O3 suffered from both a lower crystallization onset temperature Tory and a larger amount of heat liberated by crystallization and had a higher crystallization tendency contrarily, as compared with VTA-56 containing no Er2O3. Of VTA-57 to VTA-62, VTA-57 to VTA-61 having a total content of Er2O3 and La2O3 of 0.1 to 2.0 mole percent could effectively have a lower crystallization tendency. VTA-57 to VTA-63 offered no deterioration in chemical stability as compared with VTA-56 and had a glass softening point Ts of 280° C. or lower. The softening point Ts, crystallization onset temperature Tory, and amount of heat liberated by crystallization of the samples were synthetically evaluated. This demonstrated that glass compositions having a total content of Er2O3 and La2O3 of 0.1 to 1. 0 mole percent were most effective, as indicated in data of VTA-57 to VTA-60.
These data and considerations demonstrated as follows. Assume that lead-free low-melting glass compositions contain a vanadium oxide, a tellurium oxide, and a silver oxide as principal components. These lead-free low-melting glass compositions, when further containing at least one selected from yttrium oxide and lanthanoid oxides in the content of 0.1 to 3.0 mole percent, can effectively have a lower crystallization tendency. The content of at least one selected from yttrium oxide and lanthanoid oxides is more preferably 0.1 to 2.0 mole percent, and is most effectively and preferably 0.1 to 1.0 mole percent when the softening point Ts, crystallization onset temperature Tory, and amount of heat liberated by crystallization of the samples are synthetically evaluated. In addition, the glass compositions, when further containing at least one selected from BaO, WO3, and P2O5 as a secondary component, can more effectively have a still lower crystallization tendency.
Obviously, lead-free low-melting glass compositions, when further containing at least one selected from yttrium oxide and lanthanoid oxides, can have a lower crystallization tendency regardless of their glass formulations, as long as containing a vanadium oxide, a tellurium oxide, and a silver oxide as principal components. However, there can be preferred content ranges (formulation ranges) on the principal components of V2O5, TeO2, and Ag2O and on the secondary components of BaO, WO3, and P2O5, in order to expand the glass compositions into the sealing and/or bonding of glass-sealed components and electrical/electronic components and into the formation of electrodes/interconnections and conductive junctions. For the principal components, Tables 2 and 3 demonstrated that the total content of V2O5, TeO2, and Ag2O are effectively 85 mole percent or more, and the contents of TeO2 and Ag2O are each effectively 1 to 2 times as much as the content of V2O5. For the secondary component, Tables 2 and 3 also demonstrated that the glass compositions effectively contain at least one selected from BaO, WO3, and P2O5 in a content of 13 mole percent or less. The glass compositions, as having the configuration, can act as lead-free low-melting glass compositions having a softeningpoint Ts of 280° C. or lower. In addition, the glass compositions, as further containing at least one selected from yttrium oxide and lanthanoid oxides, can have a crystallization onset temperature Tory higher than the softening point Ts by 60° C. or more and can satisfactorily soften and flow at a lower temperature as compared with conventional glass compositions.
In this experimental example, low-temperature sealing glass frits each containing a lead-free low-melting glass composition according to an embodiment of the present invention and low-thermal-expansion ceramic particles were prepared. Using the frits, a pair of metal substrates, a pair of glass substrates, or a pair of ceramic substrates, each of the same kind, was bonded, and how the pair of substrates was bonded was evaluated with shear stress . The lead-free low-melting glass compositions used herein were two different glass compositions VTA-13 and VTA-32 (see Tables 2 and 3) in the form of particles. The low-thermal-expansion ceramic particles used herein were seven different particles of CF-01 to CF-07 (see Table 4). Table 4 also shows the density and coefficient of thermal expansion of the low-thermal-expansion ceramic particles. The lead-free low-melting glass compositions in Tables 2 and 3 had a density of 5.0 to 6.0 g/cm3 and a coefficient of thermal expansion of 160×10−7 to 195×10−7 per degree centigrade at temperatures in the range of room temperature to 150° C. The metal substrates used herein were aluminum (Al), silver (Ag), copper (Cu), nickel (Ni), and iron (Fe) substrates. The glass substrate was a soda-lime glass substrate, and the ceramic substrate was an aluminum oxide (Al2O3) substrate. Each evaluation sample was prepared in the following manner. Initially, a low-temperature sealing glass paste containing a lead-free low-melting glass composition in the form of particles, low-thermal-expansion ceramic particles, and a solvent was prepared. The paste was applied to each substrate, dried, and preliminarily fired. The pair of the substrates was then laminated, heated, and thereby bonded.
(Preparation of Low-Temperature Sealing Glass Paste)
A lead-free low-melting glass composition in the form of particles, low-thermal-expansion ceramic particles, and a solvent were blended, mixed, and yielded a series of low-temperature sealing glass pastes. The lead-free low-melting glass composition particles were VTA-13 and VTA-32 in the form of particles having a particle diameter of about 10 μm. The low-thermal-expansion ceramic particles were particles of: zirconium phosphate tungstate (CF-01), zirconium phosphate tungstate containing a trace amount of iron tungstate (CF-02), quartz glass (CF-03), zirconium silicate (CF-04), aluminum oxide (CF-05), mullite (CF-06), and niobium oxide (CF-07), each of which had a particle diameter of about 10 to about 30 μm. Samples to be heated and fired in an inert gas or vacuum atmosphere contained α-terpineol as the solvent and further contained isobornylcyclohexanol as a viscosity modifier. Samples to be fired in the air contained diethylene glycol n-butyl ether acetate as the solvent and further contained ethyl cellulose as a resin binder. The lead-free low-melting glass composition particles and the low-thermal-expansion ceramic particles were blended in eight different ratios (in volume percent) of 100:0, 90:10, 80:20, 70:30, 60:40, 50:50, 40:60, and 30:70 to give corresponding low-temperature sealing glass pastes. The low-temperature sealing glass pastes were prepared so as to have a solids content of about 80 mass percent. The “solids content” refers to the total content of the lead-free low-melting glass composition particles and the low-thermal-expansion ceramic particles.
(Preparation of Evaluation Sample)
Initially, a cylindrical substrate 1 including a bonding plane 2 and having a diameter of 5 mm and a thickness of 5 mm was prepared (step (a)).
Next, the bonding plane 2 of the cylindrical substrate 1 was coated with a low-temperature sealing glass paste 3 by dispensing (step (b)).
The resulting article was dried at 120° C. to 150° C. in the air. This was placed in an electric furnace, heated up to 220° C. at a rate of temperature rise of 10° C. per minute in an inert gas (nitrogen) or in the air, held for 15 minutes, heated up to a temperature higher than the softening point Ts of the contained lead-free low-melting glass composition by about 50° C. at the same rate of temperature rise as above, held for 15 minutes, and thereby formed a low-temperature sealing glass frit 4 on the bonding plane 2 of the cylindrical substrate 1 (step (c)). Specifically,theglasspastescontainingthelead-free low-melting glass compositions VTA-13 and VTA-32 were heated respectively up to 270° C. and 290° C.
The resulting article was placed on a plate substrate 5 having a thickness of 3 to 5 mm and including a material of the same type with the cylindrical substrate 1, fastened thereon with a heat-resistant clip, heated up to 270° C. or 290° C. in an inert gas (nitrogen) or in the air at a rate of temperature rise of 10° C. per minute, held for 15 minutes, and yielded a bonded article (step (d)).
The bonded article was subjected to shear stress measurement. Samples using a copper (Cu) or iron (Fe) substrate were heated in the inert gas (nitrogen) atmosphere, and samples using the other substrates were heated in the air. The blending ratio between the lead-free low-melting glass composition particles and the low-thermal-expansion ceramic particles in the low-temperature sealing glass paste, and the type of the low-thermal-expansion ceramic particles were selected in consideration of the coefficient of thermal expansion of the substrate to be bonded. The coefficients of thermal expansion of the substrates used are 224×10−7 per degree centigrade (aluminum (Al)), 197×10−7 per degree centigrade (silver (Ag)), 164×10−7 per degree centigrade (copper (Cu)), 133×10−7 per degree centigrade (nickel (Ni)), 127×10−7 per degree centigrade (iron (Fe)), 88×10−7 per degree centigrade (soda-lime glass), and 81×10−7 per degree centigrade (aluminum oxide (Al2O3)).
(Evaluation of Bonding)
Each of the bonded articles prepared using the low-temperature sealing glass pastes was examined to measure and evaluate a shear stress. In the shear stress evaluation, the sample having the shear stress of 30 MPa or more was evaluated as “excellent”, the sample having the shear stress of 20 to 30 MPa was evaluated as “good”, the sample having the shear stress of 10 to 20 MPa was evaluated as “moderate”, and the sample having the shear stress of less than 10 MPa was evaluated as “rejected”.
The results of the evaluation of the shear stress in the bonded articles including the different substrates are shown in Tables 5 to 11. The evaluation results are shown in Table 5 for bonded articles between aluminum (Al) substrates; in Table 6 for bonded articles between silver (Ag) substrates; in Table 7 for bonded articles between copper (Cu) substrates; in Table 8 for bonded articles between nickel (Ni) substrates; in Table 9 for bonded articles between iron (Fe) substrates; in Table 10 for bonded articles between soda-lime glass substrates; and in Table 11 for bonded articles between aluminum oxide (Al2O3) substrates.
With reference to Table 5, the tested bonded articles between aluminum (Al) substrates employed the low-thermal-expansion ceramic particles CF-04 or CF-05 (see Table 4) in different contents (blending amounts) of 0 to 20 volume percent and employed the lead-free low-melting glass composition VTA-13 or VTA-32 in different contents of 100 to 80 volume percent. The data demonstrated that these samples offered excellent results under all the conditions, had a very high bond strength and very good adhesion to aluminum (Al), and offered similar results even when using either of VTA-13 and VTA-32. With reference to Table 6, the bonded articles between silver (Ag) substrates also offered excellent results, and the constitutive glass frits had a very high bond strength and very good adhesion to silver (Ag), as with aluminum (Al).
With reference to Table 7, the tested bonded articles between copper (Cu) substrates employed the low-thermal-expansion ceramic particles CF-04, CF-05, and CF-06 (see Table 4) in different contents (blending amounts) of 20 to 40 volume percent and employed the lead-free low-melting glass compositions VTA-13 and VTA-32 in different contents of 80 to 60 volume percent. These samples offered good or higher results under all the conditions. The glass frits employing VTA-13, when further containing an increasing content (amount) of CF-04 or CF-06, offered a higher bond strength and better adhesion to copper (Cu). This is because the glass frits came to have a coefficient of thermal expansion conformable to that of copper (Cu). In contrast, the glass frits using CF-07 offered opposite results . This is because CF-07 has a very low coefficient of thermal expansion as compared with CF-04 and CF-06. In contrast, the samples using VTA-32 did not offer a significant difference in shear stress among blending ratios, unlike the samples using VTA-13. This is probably because the samples using VTA-32 were heated and bonded at a higher temperature, and this accelerated the oxidation of copper (Cu) by VTA-32.
With reference to Table 8, the tested bonded articles between nickel (Ni) substrates employed low-thermal-expansion ceramic particles CF-03, CF-06, and CF-07 (see Table 4) in different contents (amounts) of 30 to 50 volume percent and employed the lead-free low-melting glass compositions VTA-13 and VTA-32 in different contents of 70 to 50 volume percent. The samples offered good or higher results under all the conditions and offered similar results even when using either of VTA-13 and VTA-32. The samples using CF-03, when containing CF-03 in a content (amount) of 40 volume percent, had a highest shear stress and offered a very high bond strength and very good adhesion to the nickel (Ni) substrates. The data demonstrated that the samples using CF-06 and CF-07 in increasing contents (amounts) had a higher (increasing) shear stress and offered a higher bond strength and better adhesion to the nickel (Ni) substrates. This is probably because the samples came to have a coefficient of thermal expansion conformable to that of nickel (Ni).
With reference to Table 9, the tested bonded articles between iron (Fe) substrates employed the low-thermal-expansion ceramic particles CF-01 to CF-03 (see Table 4) in different contents (amounts) of 30 to 50 volume percent and employed the lead-free low-melting glass compositions VTA-13 and VTA-32 in different contents of 70 to 50 volume percent. The samples offered good or higher results under all the conditions and offered similar results even when using either of VTA-13 and VTA-32. The data demonstrated that the samples using CF-01 and CF-02 had a high shear stress regardless of their contents (amounts) and offered a very high bond strength and very good adhesion to iron (Fe). This is probably because as follows. CF-01 and CF-02 have coefficients of thermal expansion as ones of the lowest in the ceramic particles in Table 4 and still have good wettability with and adhesion to VTA-13 and VTA-32. The resulting low-temperature sealing glass frits can easily have efficiently lowered coefficients of thermal expansion conformable to the coefficient of thermal expansion of the iron (Fe) substrates. The data also demonstrated that the samples using CF-03 did not have so significant results as compared with the samples using CF-01 and CF-02, had an increasing shear stress, and offered a higher bond strength and better adhesion to the iron (Fe) substrate with an increasing content (amount) of CF-03. This is also because the samples came to have a coefficient of thermal expansion conformable to that of iron (Fe).
With reference to Table 10, the tested bonded articles between soda-lime glass substrates employed the low-thermal-expansion ceramic particles CF-01 and CF-02 (see Table 4) in different contents (amounts) of 40 to 70 volume percent and employed the lead-free low-melting glass compositions VTA-13 and VTA-32 in different contents of 60 to 30 volume percent. There was little difference in shear stress between CF-01 and CF-02, and between VTA-13 and VTA-32. The samples offered good or higher results under all the conditions when containing CF-01 or CF-02 in the content (amount) of 40 to 60 volume percent and VTA-13 or VTA-32 in the content (amount) of 60 to 40 volume percent. The samples, when containing CF-01 or CF-02 in a content of 50 volume percent, had a largest shear stress and offered a very high bond strength and very good adhesion to the soda-lime glass substrates. The samples, when containing CF-01 or CF-02 in the content (amount) of 60 volume percent or more, had a lower shear stress and were evaluated as rejected at a content of 70 volume percent. This is because as follows. Assume that glass frits contain VTA-13 or VTA-32 in an excessively low content (amount) with respect to the content (amount) of CF-01 or CF-02. In this case, the glass frits soften and flow unsatisfactorily as low-temperature sealing glass frits, have inferior adhesion and bonding properties to the soda-lime glass substrates, and fail to have a good shear stress. With reference to Table 11, the bonded articles between aluminum oxide (Al2O3) substrates also offered shear stress evaluation results similar to those of the bonded articles between soda-lime glass substrates. This is because the aluminum oxide (Al2O3) and soda-lime glass have coefficients of thermal expansion at similar levels. These results and considerations demonstrated that it is important to design low-temperature sealing glass frits to contain the lead-free low-melting glass composition according to the embodiment of the present invention in a content (amount) of 40 volume percent or more, and low-thermal-expansion ceramic particles in the content (amount) of 60 volume percent or less. The tested bonding between the soda-lime glass substrates and between the aluminum oxide (Al2O3) substrates employed the low-temperature sealing glass paste containing diethylene glycol n-butyl ether acetate as a solvent and ethyl cellulose as a resin binder. For further testing, bonded articles were prepared by preparing a low-temperature sealing glass paste containing α-terpineol as a solvent and isobornylcyclohexanol as a viscosity modifier instead of the above components, and performing heating in the air. The prepared bonded articles were subjected to shear stress evaluation in a similar manner and were found to readily have a higher shear stress. This is because the low-temperature sealing glass frit at the junction (bonded portion) contained smaller amounts of residual air bubbles. The data indicate that α-terpineol is as the solvent effective not only in an inert gas atmosphere, but also in the air.
These data demonstrated that the low-temperature sealing glass frit according to the embodiment of the present invention effectively contains 40 to 100 volume percent of the lead-free low-melting glass composition according to the embodiment of the present invention and 0 to 60 volume percent of the low-thermal-expansion ceramic particles. The data also demonstrated that the low-thermal-expansion ceramic particles can be selected from zirconium phosphate tungstate (Zr2(WO4) (PO4)2), quartz glass (SiO2), zirconium silicate (ZrSiO4), aluminum oxide (Al2O3), mullite (3Al2O3.2SiO2), and niobium oxide (Nb2O5) each in particle form. In particular, the low-temperature sealing glass frit more effectively contains zirconium phosphate tungstate (Zr2(WO4) (PO4)2) and/or a compound containing mainly zirconium phosphate tungstate (Zr2(WO4) (PO4)2) so as to still less undergo thermal expansion. The content of this component is preferably 30 to 50 volume percent. The low-temperature sealing glass paste according to the embodiment of the present invention may contain a solvent that can be selected from α-terpineol and diethylene glycol n-butyl ether acetate, of which α-terpineol is more effective.
In this experimental example, conductive materials containing the lead-free low-melting glass composition according to the embodiment of the present invention and metal particles were prepared. Pairs of metal substrates of the same kind were bonded using the conductive materials, and how the metal substrates were bonded was evaluated with electric resistance (contact resistance) between the metal substrates. The lead-free low-melting glass composition used herein was VTA-31 (see Tables 2 and 3), and the metal particles were four different particles of silver (Ag), copper (Cu), aluminum (Al), and tin (Sn). The metal substrates were substrates of aluminum (Al), silver (Ag), and copper (Cu). Each evaluation sample was prepared in the following manner. Initially, a conductive glass paste containing the lead-free low-melting glass composition particles, the metal particles, and a solvent was prepared. This was applied to both of a pair of the substrates, dried, preliminarily fired. The both substrates were then laminated, heated, and thereby bonded.
(Preparation of Conductive Glass Paste)
The lead-free low-melting glass composition particles, the metal particles, and the solvent were blended and mixed to give each conductive glass paste. The lead-free low-melting glass composition particles used herein were VTA-31 in the form of particles having a particle diameter of about 10 μm. The metal particles were spherical (globular) silver (Ag) particles having an average particle diameter of about 1.5 μm, spherical copper (Cu) particles having an average particle diameter of about 20 μm, spherical aluminum (Al) particles having an average particle diameter of about 10 μm, and spherical tin (Sn) particles having an average particle diameter of about 25 μm. The solvent was α-terpineol, added with isobornylcyclohexanol as a viscosity modifier. The lead-free low-melting glass composition particles and the metal particles were blended in five different blending ratios (in volume percent) of 100:0, 80:20, 60:40, 40:60, and 20:80 to prepare corresponding conductive glass pastes. The conductive glass pastes were prepared so as to have a solids content of about 80 mass percent. The “solids content” refers to the total content of the lead-free low-melting glass composition particles and the metal particles.
(Preparation of Evaluation Sample)
The contact resistance between each pair of metal substrates was measured by preparing an evaluation sample as in Experimental Example 3 by the procedure of Experimental Example 3. Specifically, this experimental example employed the evaluation sample and its preparation method similar to those illustrated in
Initially, a cylindrical metal substrate 1′ including a bonding plane 2′ and having a diameter of 5 mm and a thickness of 5 mm was prepared (step (a)).
Next, the bonding plane 2′ of the cylindrical metal substrate 1′ was coated with a low-temperature sealing glass paste 3′ by dispensing (step (b)).
The resulting article was dried at 120° C. to 150° C. in the air. This was placed in an electric furnace, heated up to 220° C. at a rate of temperature rise of 10° C. per minute in an inert gas (nitrogen or argon), held for 15 minutes, heated up to a temperature higher than the softening point Ts of the contained lead-free low-melting glass composition by about 40° C. at the same rate of temperature rise as above, held for 10 minutes, and thereby formed a low-temperature sealing glass frit 4′ on the bonding plane 2′ of the cylindrical metal substrate 1′ (step (c)). This experimental example employed the lead-free low-melting glass composition VTA-31, and the heating was performed up to a temperature of 280 ° C. that is higher than the softening point Ts by about 40° C. The resulting article was placed on a plate metal substrate 5′ having a thickness of 1 to 3 mm and including a material of the same type with the cylindrical metal substrate 1′, fastened thereon with a heat-resistant clip, heated up to 280° C. in an inert gas (nitrogen) at a rate of temperature rise of 10° C. per minute held for 30 minutes, and yielded a bonded article (step (d)).
The bonded article was subjected to measurement of contact resistance between metal substrates.
(Evaluation of Bonding)
Each of the prepared bonded articles was examined to measure contact resistance (electric resistance) between the metal substrates by the four probe method. As a comparison, bonding of metal substrates using a lead-free tin solder was also performed. The contact resistance of bonded articles bonded with the solder was 3.2×10−3 Ω/mm2 for bonding between the aluminum (Al) substrates (Al/Al bonding), 4.7×10−6 Ω/mm2 for bonding between the silver (Ag) substrates (Ag/Ag bonding), and 5.0×10−6 Ω/mm2 for bonding between the copper (Cu) substrates (Cu/Cu bonding). The Al/Al bonding had a contact resistance higher than those of the Ag/Ag bonding and the Cu/Cu bonding by about three orders of magnitude. This is because a natural oxide layer having a high electric resistance was formed on the Al substrate surfaces.
Typically, Al/Al bonding, Ag/Ag bonding, and Cu/Cu bonding were performed using conductive materials each containing the lead-free low-melting glass composition VTA-31 and Ag metal particles.
Separately, Al/Al bonding, Ag/Ag bonding, and Cu/Cu bonding were performed using conductive materials each containing the lead-free low-melting glass composition VTA-31 and Cu metal particles.
Al/Al bonding, Ag/Ag bonding, and Cu/Cu bonding were also performed using conductive materials each containing the lead-free low-melting glass composition VTA-31 and Al metal particles.
Al/Al bonding, Ag/Ag bonding, and Cu/Cu bonding were also performed using conductive materials each containing the lead-free low-melting glass composition VTA-31 and Sn metal particles.
These results and considerations demonstrate that the lead-free low-melting glass composition according to the embodiment of the present invention can be expanded into conductive materials and corresponding conductive glass pastes so as to form conductive junctions to establish connection (conduction) between metal substrates. In this experimental example, VTA-31 has been described representatively as a lead-free low-melting glass composition according to an embodiment of the present invention. Obviously, other lead-free low-melting glass compositions according to embodiments of the present invention can also develop similar performance. Likewise, Ag, Cu, Al, and Sn have been described representatively as metal particles to be contained in conductive materials or corresponding conductive glass pastes. It should be noted, however, that the present invention can provide similar performance on not only these metals, but also on alloys of them. Solder is generally applied to form a conductive junction between metal substrates. In consideration of differentiation from the solder, Ag particles and Al particles are effective as the metal particles to be contained in the conductive material or in the corresponding conductive glass paste. The solder hardly establish good conductive junction on Al substrates and other metal substrates bearing a natural oxide layer on the surface. In contrast, the conductive material and conductive glass paste according to the embodiments of the present invention can establish good conductive bonding (conductive junction) even on such metal substrates. This is archived by the action of the constitutive lead-free low-melting glass composition according to the embodiment of the present invention.
The data demonstrated that the conductive material and corresponding conductive glass paste according to embodiments of the presentinventionareveryeffectiveforthelow-temperatureformation of conductive junctions in various electronic components. When a portion to be bonded or sealed may have conductivity, the conductive material and corresponding conductive glass paste according to embodiments of the present invention are usable also as a low-temperature sealing glass frit and a corresponding low-temperature sealing glass paste as described in Experimental Example 3.
In this experimental example, conductive materials each containing a lead-free low-melting glass composition according to the embodiment of the present invention and metal particles were prepared. Using the conductive materials, an electrode/interconnection was formed on different substrates and was examined to evaluate electric resistance (interconnect resistance) and adhesion to the substrates. The lead-free low-melting glass composition and the metal particles used herein were respectively VTA-36 (see Tables 2 and 3) and silver (Ag) particles. The substrates used were an aluminum oxide (Al2O3) substrate, a borosilicate glass substrate, a silicon (Si) substrate, a ferrite substrate, and a polyimide substrate. Each evaluation sample was prepared in the following manner. Initially, a conductive glass paste containing the lead-free low-melting glass composition particles, the metal particles, and a solvent was prepared. The conductive glass paste was applied to each substrate, dried, and preliminarily fired to form an electrode/interconnection.
(Preparation of Conductive Glass Paste)
The lead-free low-melting glass composition particles, the metal particles, and the solvent were blended, mixed, and yielded a series of conductive glass pastes. The lead-free low-melting glass composition particles used herein were VTA-36 particles having a particle diameter of about 10 μm, and the metal particles were spherical silver (Ag) particles having an average particle diameter of about 1.5 μm. The solvent was α-terpineol, added with isobornylcyclohexanol as a viscosity modifier. Table 12 shows blending ratios between the lead-free low-melting glass composition VTA-36 particles and the Ag metal particles. Seven different conductive glass pastes were prepared in the blending ratios given in Table 12. The conductive glass pastes were prepared so as to have a solids content of about 80 mass percent. The “solids content” refers to the total content of the lead-free low-melting glass composition particles and the metal particles.
(Preparation of Evaluation Sample)
Using the seven conductive glass pastes DH-01 to DH-07 as in Table 12, electrodes/interconnections were formed in an interconnection pattern illustrated in
(Evaluation of Interconnect Resistance)
As described above, the interconnections 7 to 13 were formed on each substrate using the seven conductive glass pastes DH-01 to DH-07 having blending ratios given in Table 12. The interconnect resistance of each of the interconnections was measured by the four probe method.
(Evaluation of Adhesion)
The interconnections 7 to 13 were subjected to a peel test to evaluate adhesion to the substrates. A peeling tape was applied to each interconnection on the substrate and then peeled off. A sample suffering from neither peeling of the interconnection from the substrate nor break was evaluated as “accepted”. In contrast, a sample suffering from peeling and/or break in the interconnection was evaluated as “rejected”.
Typically, interconnections were formed on each substrate using conductive materials each containing the lead-free low-melting glass composition VTA-36 and the Ag metal particles.
Table 13 shows the peel test results of the interconnections formed on the substrates. The samples were evaluated as accepted and offered a good adhesion with respect to any type of the substrates at a lead-free low-melting glass composition having the VTA-36 content of 10 volume percent or more and a Ag metal particles content of 90 volume percent or less, as is demonstrated by the data of DH-02 to DH-07 in Table 13. However, the samples suffered from an interconnection peeling, were evaluated as rejected, and were considered to have an insufficient adhesion at the VTA-36 content of 5 volume percent and the Ag content of 95 volume percent. These results demonstrated that the lead-free low-melting glass composition in the conductive material satisfactorily softens and flows upon the interconnection formation and is thereby bonded to and brought into intimate contact with the substrate; but that the glass composition, if present in an excessively low content, insufficiently comes into contact with the substrate. This demonstrated that the conductive material preferably contains the lead-free low-melting glass composition in the content of 10 volume percent or more. It should be noted, however, that even a conductive material containing the lead-free low-melting glass composition in the content of 5 volume percent can sufficiently possibly offer a good adhesion if a refinement such as pressurizing upon the interconnection formation can be made.
As is demonstrated above, the lead-free low-melting glass compositions according to the embodiment of the present invention can be expanded effectively into conductive materials and corresponding conductive glass pastes to form electrodes/interconnections at a low temperature. In this experimental example, VTA-36 was used and described as a representative lead-free low-melting glass composition. Obviously, however, other lead-free low-melting glass compositions according to embodiments of the present invention can develop performance at similar levels. Likewise, the Ag particles were used in this experimental example as metal particles to be contained in conductive materials and corresponding conductive glass pastes. Also obviously, the present invention is not limited thereto and can be applied also to Ag alloys, Cu, Al, and Sn, and alloys of them. The above evaluations and considerations demonstrated that the conductive materials and corresponding conductive glass pastes according to embodiments of the present invention are very effective for the low-temperature formation of electrodes/interconnections in various electronic components.
In this experimental example, vacuum-insulating double glass panels were prepared representatively as a glass-sealed component according to an embodiment of the present invention. Specifically, the vacuum-insulating double glass panels were prepared using a pair of soda-lime glass substrates, and a low-temperature sealing glass frit according to an embodiment of the present invention. Whether and how the low-temperature sealing glass frit according to the embodiment of the present invention can be applied was evaluated. In this experimental example, a low-temperature sealing glass paste was used to form the low-temperature sealing glass frit.
As illustrated in
As illustrated in
The soda-lime glass substrates 15 and 16 used in this experimental example each had a size of 900 by 600 by 3mm. The soda-lime glass substrate 15 bore the heat-reflecting film 22, and the soda-lime glass substrate 16 included the evacuation port 20. The panel included the spherical beads 19 having a diameter of a little under 200 μm in the seal portion 14 and the spacers 18 so as to allow the distance between the soda-lime glass substrates 15 and 16, namely, the thickness of the space 17, to be about 200 μm. The spherical beads 19 included soda-lime glass. The low-temperature sealing glass frit used in the seal portion 14 included the lead-free low-melting glass composition VTA-39 (see Tables 2 and 3) and the low-thermal-expansion ceramic particles CF-01 (see Table 4) in a blending ratio in volume percent of 50:50. The spherical beads 19 were contained in the seal portion 14 in a content of 1 volume percent with respect to the volume of the low-temperature sealing glass frit; and were contained in the spacers 18 in a content of 20 volume percent with respect to the volume of the low-temperature sealing glass frit.
(Preparation of Low-Temperature Sealing Glass Paste)
The lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, the low-thermal-expansion ceramic particles, and a solvent were blended, mixed, and yielded low-temperature sealing glass pastes. The lead-free low-melting glass composition particles used herein were VTA-39 particles having a particle diameter of about 10 μm; and the low-thermal-expansion ceramic particles were CF-01 (zirconium phosphate tungstate) particles having a particle diameter of about 30μm. Thesolventwas α-terpineol,addedwithisobornylcyclohexanol as aviscositymodifier. Thelead-freelow-meltingglasscomposition particles VTA-39 and the low-thermal-expansion ceramic particles CF-01 were blended in a ratio in volume percent of 50:50, and the low-temperature sealing glass pastes were prepared so as to have a solids content of 75 to 80 mass percent, where the “solids content” refers to the total content of VTA-39 and CF-01. The low-temperature sealing glass pastes further contained soda-lime glass spherical beads having a particle diameter of about 180 to about 200 μm in a content of 1 volume percent for the low-temperature sealing use and 20 volume percent for the spacers. The contents herein are each with respect to the solids content.
(Preparation of Vacuum-Insulating Double Glass Panel)
The vacuum-insulating double glass panel was prepared in this experimental example by a method that will be described with reference to
As illustrated in
As illustrated in
With reference to
According to the sealing temperature profile in
As illustrated in
(Evaluation Results of Prepared Vacuum-Insulating Double Glass Panels)
Initially, the ten vacuum-insulating double glass panels prepared in this experimental example were visually inspected. As a result, they were found to have no visual defects such as fracture or cracking. The spherical beads 19 in the seal portion 14 and in the spacers 18 allowed the soda-lime glass substrates 15 and 16 to be held at an approximately uniform distance (thickness of the space therebetween). Specifically, the obtained vacuum-insulating double glass panel had a predetermined space 17. The panel was further subjected to a helium leak test and was found that the panel inside was maintained under vacuum, and the panel peripheral portion was hermetically sealed.
For the determination of the reliability of the seal portion 14, three of the prepared vacuum-insulating double glass panels were immersed in warm water at 50° C. for 30 days. Asa result, it was found that the inside of all the three panels could be maintained under vacuum without migration of water thereinto. Other three of the vacuum-insulating double glass panels were subjected to 1000 cycles of a thermal cycle test in the range of −50° C. to +100° C. Also in this test, all the three panels could maintain the inside under vacuum. These results demonstrated as follows. Assume that the low-temperature sealing glass frit and/or corresponding low-temperature sealing glass paste according to the embodiment of the present invention is applied to a vacuum-insulating double glass panel. In this case, the vacuum-insulating double glass panel can include a seal portion offering satisfactory thermal insulation and having high reliability. In addition, the low-temperature sealing glass frit and/or corresponding low-temperature sealing glass paste according to the embodiment of the present invention, when used, enables sealing to be performed at a remarkably low temperature and can significantly contribute to better productivity of such vacuum-insulating double glass panels.
As above, a vacuum-insulating double glass panel has been described in this experimental example representatively as a glass-sealed component according to an embodiment of the present invention. Specifically, the low-temperature sealing glass frit and/or corresponding low-temperature sealing glass paste containing the lead-free low-melting glass composition according to the embodiment of the present invention was applied to the vacuum-insulating double glass panel. The results demonstrated that the low-temperature sealing glass frit and corresponding low-temperature sealing glass paste containing the lead-free low-melting glass composition according to the embodiment of the present invention can be effectively applied to a seal portion of a glass-sealed component and provides a glass-sealed component having reliabilityandproductivitybothatsatisfactorylevels. Obviously, the glass frit and corresponding glass paste can be effectively expanded also into glass-sealed components other than the vacuum-insulating double glass panel.
In this experimental example, a display was prepared representatively as a glass-sealed component according to the embodiment of the present invention. Whether and how the low-temperature sealing glass frit according to the embodiment of the present invention is applicable was determined and evaluated. The display included a multiplicity of organic light-emitting diodes (OLEDs) between a pair of borosilicate glass substrates. This experimental example employed a low-temperature sealing glass paste to form the low-temperature sealing glass frit.
With reference to
The OLEDs 25 are susceptible to deterioration by the presence of water and/or oxygen. To prevent this, it is important for the peripheral portion, i.e., the seal portion 14 of the borosilicate glass substrates 23 and 24 to be hermetically sealed with the low-temperature sealing glass frit containing the lead-free low-melting glass composition according to the embodiment of the present invention. The low-temperature sealing glass frit according to the embodiment of the present invention used in the seal portion 14 contains, in addition to the lead-free low-melting glass composition according to the embodiment of the present invention, low-thermal-expansion ceramic particles so as to have a coefficient of thermal expansion conformable to the coefficient of thermal expansion of the borosilicate glass substrates 23 and 24 as much as possible. The low-temperature sealing glass frit to be applied to the seal portion 14 in this experimental example included the lead-free low-melting glass composition VTA-35 (see Tables 2 and 3) and the low-thermal-expansion ceramic particles CF-02 (see Table 4) in a ratio in volume percent of 45:55. The low-temperature sealing glass frit in this experimental example was formed from a low-temperature sealing glass paste further containing high viscosity α-terpineol as a solvent.
(Preparation of Low-Temperature Sealing Glass Paste)
The lead-free low-melting glass composition according to the embodiment of the present invention in the form of particles, the low-thermal-expansion ceramic particles, and the solvent were blended, mixed, and yielded the low-temperature sealing glass paste. The lead-free low-melting glass composition particles used herein were VTA-35 particles having an average particle diameter of about 1 μm, and the low-thermal-expansion ceramic particles were CF-02 particles having an average particle diameter of about 3 μm. CF-02 is a compound including mainly zirconium phosphate tungstate. The solvent was α-terpineol, added with isobornylcyclohexanol as a viscosity modifier. The low-thermal-expansion ceramic particles CF-02 contained iron tungstate (FeWO4) in the zirconium phosphate tungstate particles so as to efficiently absorb a red semiconductor laser beam to thereby generate heat, as described later. The low-temperature sealing glass paste was prepared so as to contain the lead-free low-melting glass composition VTA-35 particles and the low-thermal-expansion ceramic particles CF-02 in a blending ratio in volume percent of 45:55 and to have a solids content of about 80 mass percent, where the “solids content” refers to the total content of VTA-35 and CF-02.
(Preparation of Organic Light-Emitting Diode (OLED) Display)
The OLED display in this experimental example was prepared by a method as illustrated in
As illustrated in
As illustrated in these figures, a multiplicity of OLEDs 25 was formed on the borosilicate glass substrate 24. The number of the OLEDs 25 corresponds to the number of picture elements. As illustrated in
In this experimental example, five OLED displays were prepared in the above manner. The sealing was performed using the laser beam so as to prevent or mitigate thermal damage on the OLEDs and to provide better productivity.
(Evaluation Results of Prepared Organic Light-Emitting Diode (OLED) Displays)
Initially, one of the prepared OLED displays was subjected to a lighting test and found to properly illuminate. The sample OLED display also had good adhesion and bonding properties in the seal portion. Next, the OLED display was subjected to a high-humidity/temperature test (saturated pressure cooker test) at 120° C., 100% relative humidity, and 202 kPa for one day, 3 days, and 7 days. As a comparative example, an OLED display including a portion sealed with a resin was also subjected to the test. The resin-sealed portion had a line width of about 5 mm and a thickness of about 15 μm. Both the OLED displays properly illuminated in the one-day high-humidity/temperature test, but the resin-sealed OLED display suffered from significant deterioration in illumination in 3-day and longer high-humidity/temperature tests. This is because water and/or oxygen migrated from the resin-sealed portion into the OLED display and impaired the OLEDs. In contrast, the OLED display according to the embodiment of the present invention did not suffer from deterioration in illumination of the OLEDs and had good test results even in the 7-day high-humidity/temperature test. The result indicated that the OLED display can maintain good hermeticity. In addition, the OLED display after the high-humidity/temperature test was examined to evaluate the adhesion and bonding properties of the seal portion and was found to offer not so significant deterioration as compared with the resin-sealed OLED display and to have adhesion and bonding properties similar to those before the test.
As above, the organic light-emitting diode (OLED) display has been described in this experimental example representatively as a glass-sealed component according to an embodiment of the present invention. Specifically, the low-temperature sealing glass frit and corresponding low-temperature sealing glass paste each containing the lead-free low-melting glass composition according to the embodiment of the present invention were applied to the OLED display. The results demonstrated that the low-temperature sealing glass frit and corresponding low-temperature sealing glass paste each containing the lead-free low-melting glass composition according to the embodiment of the present invention can be effectively applied to a seal portion of a glass-sealed component and provides a glass-sealed component having high functions including reliability and being obtained with excellent productivity. In addition, the results of the experimental example obviously demonstrate that the glass frit and corresponding glass paste can also be expanded into glass-sealed components that are susceptible to thermal damage. Such glass-sealed components are exemplified by lighting apparatuses bearing OLEDs; and organic solar cells.
In this experimental example, a solar cell including silicon (Si) substrates having pn bonding was prepared representatively as an electrical/electronic component according to an embodiment of the present invention. Whether and how a conductive material according to an embodiment of the present invention is applicable to electrodes/interconnections of the solar cell was examined and evaluated. The conductive material in this experimental example was formed using a conductive glass paste.
As illustrated in
As illustrated in
As illustrated in
In this experimental example, the silicon substrate 27 including the pn junction was a solar-cell-use single-crystal silicon substrate having a size of 150 by 150 by 0.2 mm. In addition, a silicon nitride (SiN) antireflection film 31 was formed on the light-receiving surface of the silicon substrate 27 . The antireflection film 31 hada thickness of about 100 nm. The front electrodes/interconnections 28 and the output electrodes/interconnections 30 were formed using a conductive material. The conductive material contained the lead-free low-melting glass composition VTA-01 (see Table 1) and spherical silver (Ag) particles having an average particle diameter of about 1.5 μm in a blending ratio in volume percent of 15:85. The collector electrode/interconnection 29 was formed using another conductive material. This conductive material contained the lead-free low-melting glass composition VTA-02 (see Table 1) and spherical aluminum (Al) particles having an average particle diameter of about 3 μm in a blending ratio in volume percent of 10:90.
(Preparation of Conductive Glass Paste)
The lead-free low-melting glass composition according to the embodiment of the present invention VTA-01 or VTA-02 in the form of particles, the silver (Ag) or aluminum (Al) metal particles, and a solvent were blended, mixed, and yielded conductive glass pastes. The conductive glass paste to form the front electrodes/interconnections 28 and the output electrodes/interconnections 30 employed VTA-01 particles having an average particle diameter of about 1 μm and spherical Ag particles having an average particle diameter of about 1.5 μm in a blending ratio in volume percent of 15:85. The solvent used was α-terpineol, added with isobornylcyclohexanol as a viscosity modifier. The conductive glass paste to form the collector electrode/interconnection 29 employed VTA-02 particles having an average particle diameter of about 1 μm and spherical Al particles having an average particle diameter of about 3 μm in a blending ratio in volume percent of 10:90. The solvent used was α-terpineol, added with isobornylcyclohexanol as a viscosity modifier. Each of the conductive glass pastes had a solids content of about 80 mass percent, where the “solids content” refers to the total content of the lead-free low-melting glass composition particles and the metal particles.
(Preparation of Solar Cell)
The solar cell as illustrated in
The silicon substrate 27 (150 by 150 by 0.2 mm) used herein bore the antireflection film 31 on the light-receiving surface. The above-prepared conductive glass paste containing VTA-01 particles and Ag particles was applied to the light-receiving surface of the silicon substrate 27 by a screen process printing and dried at 120° C. to 150° C. This was heated in a tunnel furnace up to 220° C. at a rate of temperature rise of about 20° C. per minute, held for 10 minutes, further heated up to 280° C. at the same rate of temperature rise as above, and held for 5 minutes to form the front electrodes/interconnections 28 on the light-receiving surface of the silicon substrate 27. Next, the above-prepared conductive glass paste containing VTA-01 particles and Ag particles was applied to the rear surface of the silicon substrate 27 by the screen process printing and dried at 120° C. to 150° C. The above-prepared conductive glass paste containing VTA-02 particles and Al particles was applied by the screen process printing and dried at 120° C. to 150° C. This was fired under the same heating conditions as in the formation of the front electrodes/interconnections 28 and thereby formed the collector electrode/interconnection 29 and the output electrodes/interconnections 30 on the rear surface of the silicon substrate 27. The front electrodes/interconnections 28 received two thermal hystereses. This allowed the front electrodes/interconnections 28 to have good electrical connection to the silicon substrate 27. The front electrodes/interconnections 28, collector electrode/interconnection 29, and output electrodes/interconnections 30 were formed in the above manner and yielded a solar cell according to an embodiment of the present invention . In this experimental example, ten solar cells were prepared in the above manner.
(Evaluation Results of Prepared Solar Cells)
Initially, the ten solar cells prepared in this experimental example were visually inspected. Asa result, the silicon substrate 27, as well as the front electrodes/interconnections 28, collector electrode/interconnection 29, and output electrodes/interconnections 30 formed on the silicon substrate 27, offered no defects such as fracture and cracking, no significant warpage, and no appearance disadvantages. This effect was achieved by the lead-free low-melting glass compositions according to the embodiments of the present invention. Specifically, the electrodes/interconnections could be formed at a significantly low temperature. Next, the prepared ten solar cells were further examined and found to have electrical connection between the silicon substrate 27 and the front electrodes/interconnections 28 and to establish ohmic contact between the silicon substrate 27 and the collector electrode/interconnection 29 and between the silicon substrate 27 and the output electrodes/interconnections 30. The ten solar cells were further examined using a solar simulator to evaluate the generation efficiency. As a result, the solar cells were found to have a generation efficiency of about 18% as high as the generation efficiency of conventional equivalents, even though the solar cells were prepared at a remarkably low temperature. To determine the reliability, three of the prepared solar cells were immersed in warm water at 50° C. for 5 days and examined to measure the generation efficiency in a similar manner as above. The conventional solar cell suffered from corrosion of the electrodes/interconnections and had significantly lower generation efficiency of about 12% to about 13%. In contrast, the solar cells prepared in this experimental example little suffered from corrosion of the electrodes/interconnections and offered approximately no deterioration in generation efficiency. This is probably because the specific reaction of the lead-free low-melting glass composition according to the embodiment of the present invention with Ag or Al can give solar cells having such high reliability, as described in Experimental Example 4.
Next, an overlap portion of the collector electrode/interconnection 29 and the output electrodes/interconnections 30 on the rear surface was disintegrated and examined. As a result, the overlap portion was found to include no brittle intermetallic compound that is formed by the reaction between Ag and Al. Thus, the silicon substrate 27 came to resist defects such as cracking even when receiving stress in a focused manner. In addition, the silicon substrate 27 significantly less suffered from warpage, and this contributed less failure of the solar cell when handled typically upon assemblage into a module. Thus, the brittle intermetallic compounds were prevented from forming and the solar cell less suffered from warpage. This is because the solar cell according to the embodiment of the present invention can be fired at a significantly low temperature (280° C.) as compared with the firing temperatures (500° C. to 800° C.) of the conventional solar cells.
As above, the solar cell has been described in this experimental example representatively as an electrical/electronic component according to an embodiment of the present invention. Specifically, the solar cell included electrodes/interconnections formed using the conductive material and corresponding conductive glass paste each containing the lead-free low-melting glass composition according to the embodiment of the present invention. The conductive material and corresponding conductive glass paste each containing the lead-free low-melting glass composition according to the embodiment of the present invention can be effectively applied to electrodes/interconnections of not only such solar cells, but also various electrical/electronic components. The conductive material and corresponding conductive glass paste can provide electrical/electronic components that have higher functions such as reliability and excel typically in productivity and yield.
In this experimental example, a quartz resonator package was prepared representatively as an electrical/electronic component according to an embodiment of the present invention. Whether and how the conductive material and the low-temperature sealing glass frit according to embodiments of the present invention are applicable to conductive junctions and/or seal portions of the package was examined and evaluated. In this experimental example, the conductive material and the low-temperature sealing glass frit were formed respectively using a conductive glass paste and a low-temperature sealing glass paste.
The quartz resonator package illustrated in
The quartz resonator package is prepared in the following manner.
Initially, the ceramic substrate 33 bearing the interconnections 34 is prepared (
The quartz resonator 32 is arranged on the conductive junctions 35 (
Independently, the ceramic cap 36 is prepared (
The ceramic substrate 33 bearing the quartz resonator 32 and the conductive junctions 35 (see
The process may be performed carefully so as to prevent the conductive junctions 35 from separating from the quartz resonator 32 and the interconnections 34. For this reason, the ceramic cap 36 and the ceramic substrate 33 are preferably sealed at a temperature equal to or lower than the softening point of the lead-free low-melting glass composition in the conductive junctions 35. Specifically, the lead-free low-melting glass composition to be contained in the low-temperature sealing glass paste preferably differs from, and has a softening point lower than, the lead-free low-melting glass composition to be contained in the conductive glass paste. The two lead-free low-melting glass compositions may have a difference in softening point between them of 20° C. or higher, and preferably 40° C. or higher.
(Preparation of Conductive Glass Paste and Low-Temperature Sealing Glass Paste)
In this experimental example, the lead-free low-melting glass composition to be contained in the conductive glass paste was VTA-16 having a softening point of 280° C. (see Tables 2 and 3); and the lead-free low-melting glass composition to be contained in the low-temperature sealing glass paste was VTA-33 having a softening point of 240° C. (see Tables 2 and 3). VTA-16 and VTA-33 have a difference in softening point of 40° C. and enable sealing without problems such as separation of the conductive junctions 35. This means that the conductive junctions 35 and seal portion 37 both at satisfactorily levels can be obtained at once.
Initially, particles of a lead-free low-melting glass composition according to an embodiment of the present invention, metal particles, and a solvent were blended, mixed, and yielded the conductive glass paste for the formation of the conductive junctions 35. The lead-free low-melting glass composition particles used herein were VTA-16 particles having an average particle diameter of about 3 μm; the metal particles were spherical silver (Ag) particles having an average particle diameter of about 1.5 μm; and the solvent was α-terpineol. The paste was further added with isobornylcyclohexanol as a viscosity modifier. The VTA-16 particles and the Ag particles were blended in a ratio in volume percent of 30:70. The conductive glass paste was prepared so as to have a solid content of about 80 mass percent, where the “solids content” refers to the total content of VTA-16 and Ag.
Separately, particles of a lead-free low-melting glass composition according to an embodiment of the present invention, low-thermal-expansion ceramic particles, and a solvent were blended, mixed, and yielded the low-temperature sealing glass paste for the formation of the seal portion 37. The lead-free low-melting glass composition particles used herein were VTA-33 particles having an average particle diameter of about 3 μm; the low-thermal-expansion ceramic particles were CF-01 (zirconium phosphate tungstate) particles having an average particle diameter of about 10 μm (see Table 4); and the solvent was α-terpineol. The paste was further added with isobornylcyclohexanol as a viscosity modifier. The VTA-33 particles and the CF-01 particles were blended in a ratio in volume percent of 70:30. The low-temperature sealing glass paste was prepared so as to have a solids content of about 80 mass percent, where the “solids content” refers to the total content of VTA-33 and CF-01.
(Preparation of Quartz Resonator Package)
The quartz resonator package was prepared in this experimental example by a method that will be illustrated specifically below. The ceramic substrate 33 and the ceramic cap 36 used in this experimental example were both made of aluminum oxide (α-Al2O3).
The prepared conductive glass paste was applied onto the interconnections 34 in the ceramic substrate 33 by dispensing and dried at 120° C. to 150° C. in the air (
Next, the quartz resonator 32 was arranged on the formed conductive junctions 35, heated up to 330° C. at a rate of temperature rise of 20 ° C. per minute in an inert gas (argon), and held for 10 minutes to connect the quartz resonator 32 to the conductive junctions 35 (
Independently, the prepared low-temperature sealing glass paste was applied to the peripheral portion of the ceramic cap 36 by the screen process printing and dried at 120° C. to 150° C. in the air (
The ceramic cap 36 bearing the seal portion 37 was arranged so as to face the ceramic substrate 33 connected to the quartz resonator 32. The resulting article was placed in a dedicated fixture and applied with a load (
(Evaluation Results of Prepared Quartz Resonator Packages)
Initially, eighteen of the quartz resonator packages prepared in this experimental example were visually inspected using a stereoscopic microscope. As a result, the packages offered little misregistration of the ceramic cap 36 upon sealing, did not offer defects such as denitrification due to crystallization, fracture, and cracking in the seal portion 37, and had no defects in appearance.
Next, whether the conductive junctions 35 in the sealed ceramic cap 36 was electrically connected to the quartz resonator 32 and to the interconnections 34 was examined by a conduction test from the interconnections 34 on the rear surface of the ceramic substrate 33. The results verified that the quartz resonators went into action in all the prepared quartz resonator packages. In addition, five of the prepared quartz resonator packages were subjected each to a helium leak test and were found that the package inside was maintained under vacuum, and the peripheral portion was hermetically sealed with the seal portion 37. To verify the reliability of the seal portion 37, five of the prepared quartz resonator packages were each subjected a high-humidity/temperature test (saturated pressure cooker test) at 120° C., 100% relative humidity, and 202 kPa for 3 days. The samples were subjected to the helium leak test again and were found that all the quartz resonator packages after the high-humidity/temperature test maintained the hermeticity and adhesion of the seal portion 37.
The results demonstrated as follows. Assume that a conductive material and/or a corresponding conductive glass paste each containing a lead-free low-melting glass composition according to an embodiment of the present invention is applied to a conductive junction; and that a low-temperature sealing glass frit and/or a corresponding low-temperature sealing glass paste each containing a lead-free low-melting glass composition according to an embodiment of the present invention is applied to a seal portion. This can give quartz resonator packages that have high reliability after consideration of influence on the environmental burden. In this experimental example, the conductive material and others are applied to a quartz resonator package representatively as an electrical/electronic component and a glass-sealed component according to an embodiment of the present invention. Obviously, however, the conductive material and corresponding conductive glass paste, low-temperature sealing glass frit, and corresponding low-temperature sealing glass paste according to embodiments of the present invention can be effectively expanded not only into such quartz resonator packages, but also into many of electrical/electronic components and glass-sealed components each including a conductive junction and/or a seal portion.
In Experimental Examples 6 to 9, the vacuum-insulating double glass panels, OLED displays, solar cells, and quartz resonator packages have been described representatively as glass-sealed components and electrical/electronic components according to embodiments of the present invention. Obviously, however, the present invention is not limited to these examples and can be applied to many of glass-sealed components and electrical/electronic components such as image display devices, personal digital assistants, IC ceramic packages, semiconductor sensors, multilayer capacitors, LEDs, and multilayered circuit boards.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2014-175580 | Aug 2014 | JP | national |
