TW200403764A - Low metal porous silica dielectric for integral circuit applications - Google Patents

Low metal porous silica dielectric for integral circuit applications Download PDF

Info

Publication number
TW200403764A
TW200403764A TW092108111A TW92108111A TW200403764A TW 200403764 A TW200403764 A TW 200403764A TW 092108111 A TW092108111 A TW 092108111A TW 92108111 A TW92108111 A TW 92108111A TW 200403764 A TW200403764 A TW 200403764A
Authority
TW
Taiwan
Prior art keywords
composition
group
film
item
patent application
Prior art date
Application number
TW092108111A
Other languages
Chinese (zh)
Inventor
Roger Y Leung
Eric Deng
Songyuan Xie
Victor Y Lu
Original Assignee
Honeywell Int Inc
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from PCT/US2002/015256 external-priority patent/WO2003088344A1/en
Application filed by Honeywell Int Inc filed Critical Honeywell Int Inc
Publication of TW200403764A publication Critical patent/TW200403764A/en

Links

Landscapes

  • Formation Of Insulating Films (AREA)

Abstract

The invention relates to the production of nanoporous silica dielectric films and to semiconductor devices and integrated circuits comprising these improved films. The nanoporous films of the invention are prepared using silicon containing pre-polymers and are prepared by a process that allows crosslinking at lowered gel temperatures by means of a metal-ion-free onium or nucleophile catalyst.

Description

200403764 玖、發明說明: 【發明所屬之技術領域】 本發明係關於奈米多孔性石夕石介電質薄膜之製造,且關 於包括此等改善之薄膜之半導體裝置及積體電路。本發明 之奈米多孔性薄膜係使用含矽之預聚合物製備,且藉由在 低膠凝溫度下,藉由不含金屬離子之鏘或親核性觸媒交聯 之方法製備。 【先前技術】 未來積體電路之尺寸會降低至低於0.15微米以下,使因連 接RC之延遲,功率之損耗及訊號交互影響造成之問題變得 更不容易解決,相信間隔之介電質(ILD)及金屬間之介電質 (IMD)應用之整合低介電質材料可協助解決此等問題。雖然 先前已努力對積體電路提供低介電質材料,但技藝中仍長 期需要進一步改善加工方法且使積體電路之製造中所用之 該材料之介電質及機械性質二者為最佳。 其一類具有低介電常數之材料為藉由旋轉溶膠凝膠技術 ,自含矽之預聚物製備之奈米多孔性矽石薄膜。空氣之介 電常數為1,且當空氣進入具有奈米尺寸之孔隙結構之適用 矽石材料中時,可製備出具有相對低介電常數(“k”)之薄膜 。奈米矽石材料受矚目係因為類似之前驅物,包含有機取 代之矽烷,如使用四乙醯氧基矽烷(TAS)/甲基三乙醯氧基矽 烷(MTAS)-衍生之矽聚合物作為基礎基質,且用於目前所用 之矽石(Si02)之玻璃上旋轉塗佈(“S.O.G”)及化學蒸氣沉積 (“CVD”)。該物質具有經證明之高機械強度,如模數及分布 84564 200403764 抓取數據所示。機械性質可藉 寸分布控制。奈米多孔性二:二性薄膜之空隙尺 寸可控制,且因此可控制所得薄膜::目:因為其孔隙尺 及介電常數。除低k外,奈米薄 :在度、機械強度 達赋之熱…點包含 至少比積體電路之微電子特性低=寸了=寸之大小 - 、’及,可由如半導晋渔库 使用之碎石及四乙氧输陶)製備;可使:生 碎石之介電常數在絲圍中“調整”;且奈米多孔料= 沉和可使用與-般S.aG.加工所用類似之設備達成。 因此,矽石材料中之高孔隙度兩 式之相同材料,另_優^可# =包吊數低於播孔隙形 奈米多孔性薄膜’且改變材料之相對密度。其他材料= 包含需要所有孔隙實質上小Μ路特性之尺寸,需要= 因孔隙度造成之強度下降’及其介電常數及環境上相關之 安定性之表面化學之作用。 密度(或者孔隙度)為控制材料介電常數之奈米薄膜之主 要參數、’JL該性質可在連續之圖譜上輕易的改變,由孔隙 度100%之極大空氣間隙至孔隙度為〇%之密實矽石。當孔隙 度增加時,介電常數及機械強度會增加,但孔隙度下降, 等。此建議奈米多孔性薄膜之密度範圍需在期望應用之所 需低介電常數範圍及機械性質間最適的均衡。 奈米多孔性矽石薄膜先前已經以許多方法製造。例如, 奈米^孔丨生薄膜已經使用溶劑及矽石前驅物之混合物製備 ,該混合物係沉積在適用之基材上。通常,將例如坡璃上 84564 200403764 旋轉塗佈形式之前驅物加於基材上,接著依形成包括奈米 孔隙之介電質薄膜形式之方式聚合。 當以例如旋轉塗佈形成該奈米多孔性薄膜時,薄膜塗層 一般係以酸性或鹼性觸媒及水催化,在起始加熱之過程中 造成聚合/膠凝(“老化”)。未經由選擇孔隙尺寸獲得最大強 度’因此使用低分子量成孔劑。 美國專利第5,895,263號敘述在基材例如晶圓上,藉由塗佈 包括可分解之聚合物及有機聚氧化矽(亦即包含縮合或聚合 义矽聚合物)之組合物,加熱該組合物使聚氧化矽進一步縮 合,且分解可分解之聚合物形成多孔性介電質層形成奈^ 多孔性矽石介電質薄膜。該方法與許多先前用於在半導體 上形成奈米多孔性薄膜之方法相似,具有f在老化或縮合 過程中及移除聚合物形成奈米多孔性薄膜中加熱之缺點。 而且,其缺點為前驅物溶液中所含之有機聚矽石會在製備 溶液後使分子量增加,因此,在儲存過程中使該ς驅物溶 以黏度增加’ JL由該儲存溶液製備之薄 =错存時間增加而增加。有機聚以之不安W因^ 且的储存時間、冷卻儲存及精密的調整輯參數, 微積體電路製造過程中達到—致之薄膜性質。 ,W多孔性結構之形成依賴之條件為成 材料之交聯溫度(或膠凝溫度)。經發現低於^ = 離子如:二L7孔性結構在溶液上旋轉中之驗性陽 符合Ic岸用中' ppb水準下無法製造。然而,需 …中《低金屬濃度迫切之需求一般之實務為在 84564 200403764 4液上旋轉之金屬濃度低於5〇 ppb。因此,需要發展一種可 持續提供低於2.5之介電常數且孔隙尺寸之直徑低於1〇㈣之 低金屬奈米多孔性矽石薄膜。如今已經發現藉由使用鏘離 子或親核物,可在低金屬旋轉調配物中低溫下形成多孔性 矽石網路。鑕離子或親核物之作用為降低膠凝溫度,因可 在移除成孔劑前使硬質網路硬化,因此在不需要不期望之 驗性離子下製造奈米多孔性薄膜。 【發明内容】 本發明係提供一種製造奈米多孔性矽石介電質薄膜之方 法,包括 ⑷製備包括切預聚物、成孔劑、及選自包含鑕化合物及 親核物之無金屬離子觸媒之組合物; (b) 以組合物塗佈基材,形成薄膜; (c) 使組合物交聯,產生膠凝薄膜,及 ⑷在溫度下及有效期間使膠凝薄膜加熱,移除實質上所有 該成孔劑。 本各月亦棱供一種包括含預聚物、成孔劑及選自由鐳化 合物及親核物組成之群組之觸媒之組合物。 本I凡上k供一種降低形成多孔性矽石薄膜時之溫度下 P奪《方法,包括〈步驟為將鏘離子或親核物加於含石夕之預 聚物及成孔劑中。 【實施方式】 以下之奈米多孔性矽石介 備。通常,,以矽為主之介 據此,介電常數或k值約為3或 電質薄膜均可以本發明之方法製 84564 200403764 ^膜(包含奈米多孔性碎石介電質薄 ^及可為鑕化合物或親核物之無金屬離子之觸成 通用切預聚物之组合物製備。亦可包本一種=摻合-疋溶劑及/或其他成分。介 4夕種選用 藝中已知之方法,塗你、=田 藉由任何技 裝η μΓ 佈通用之基材上,例如製造半導骨番 ,置如積體電路(“IC,,)用之基材,形導: 熱使組合物交聯,形成 要耆猎由如加 較^下Η 再使經膠凝之薄膜在 同/皿下加熱,霄質的移除所有成孔劑。 以:發明之方法製備之薄膜具有許多優 知《優點,包含改善之機械強度,其可製造可承受 理之基材上製備半導 、工處 千等裝置所需進-步加工步驟之薄膜, =且穩定之介電常數。穩定介電常數之性質可在不需如 t許多形成奈米多孔性石夕石介電質薄膜之方法所需般之 步表面改質步驟下有利的達成。另外’以本發明方法 產生W石介薄膜可如起初形成般之足夠的疏水性。 再者’本發明之方法針對塗佈之預聚物組合物之起始聚 t(亦即膠凝或老化)有利的需要相對低溫。本發明之方法 2奈米規格直徑之孔隙尺寸,其尺寸分布亦均勾。所得 ,米多孔性矽石薄膜之介電常數一般約為3或以下,更通常 約⑷.3至約3.〇 ’且最通常為約h7至約2·5。薄膜之平均孔隙 直=通常約為1脆至約30贈,更好約為1 nm至約1()nm,且 ^常約為lnm至約5nm。薄膜之孔隙體積以薄膜全部體積為 準’一般為約5%至約80%。 應了解奈米多孔性介電薄膜一詞係指以本發明之方法, 84564 -10- /64 由有機或無機坡璃基質材料(例如任何適用之以硬為主 :)製備之介電質薄膜。另夕卜“老化”係指基材上之合併以 夕石為主之别驅物組合物於沉積後之 “硬化詞係指移㈣留之·0H)基,移除水 、及在微兒子製造法之後續加工過程中製ϋ更安定薄膜之 万法。硬化製程係在膠凝後進行,且一般係藉由加熱進行 ,但可使用任何其他技藝上已知之硬化形式,例如藉由施 加電子束、紫外線輻射等形式之能量。 、、介電質薄膜例如間隔之介電質塗層係由塗佈於基材上之 適口組合物製備。塗体介電質前驅物組合物之技藝中已知 ,方法包含(但不限)旋轉塗佈、浸潰塗佈、刷塗了滾塗二 :、佈=/或化學备氣沉積。在塗佈此等材料型形成介電質薄 " 土材表面可視情況針對塗層,以標準、技蓺中已 7之清潔方法製備。塗層在經加工,以達到期望類;以及 舁:電質塗層相符,其中之加工步驟係經選擇以適合選用 ::驅物以及期望<最終產物。本方法及組合物之其他細 即如下。 中所用 < 基材,,包含在本發明之奈切石薄膜塗佈 边占 般為適用於製造積體電路切晶圓,且形成奈米多 孔切石薄膜之基礎材料係藉由一般之方法塗体於基材上 喷=(但不限)旋轉塗怖、浸潰塗佈、刷塗、滾塗、及/或 塗佈基礎材料形成奈米多孔性石夕石薄膜之前,基材 表面可视情況以標準、技藝中已知之清潔方法製備。 84564 • 11 - 200403764 本發明週用之基材包含半導體基材,如砷化鎵(“GaAs”)、 矽及含矽之組合物如結晶矽、聚矽、無定型矽、取向接長 之矽,及二氧化矽(“Si〇2,,)及其混合物。 基材<表面上為選用之產生線條之圖案,如金屬、氧化 物 '虱化物或氧基氮化物線條,其可藉由習知之微影蝕刻 技術形成。該線條之適用材料包含氧化㈣200403764 (1) Description of the invention: [Technical field to which the invention belongs] The present invention relates to the manufacture of nano-porous lithospar dielectric films, and to semiconductor devices and integrated circuits including these improved films. The nanoporous film of the present invention is prepared using a silicon-containing prepolymer, and is prepared at a low gelation temperature by a method that does not contain metal ions or a nucleophilic catalyst. [Previous technology] In the future, the size of integrated circuits will be reduced to less than 0.15 micrometers, which will make it more difficult to solve the problems caused by the delay of RC connection, power loss and signal interaction. I believe the dielectric properties of the interval ( Integrated low-dielectric materials (ILD) and inter-metal dielectric (IMD) applications can help solve these problems. Although previous efforts have been made to provide low-dielectric materials for integrated circuits, there is still a long-term need in the art to further improve processing methods and optimize both the dielectric and mechanical properties of the materials used in the manufacture of integrated circuits. One type of material with a low dielectric constant is a nano-porous silica film prepared from a silicon-containing prepolymer by a spin sol-gel technique. The dielectric constant of air is 1, and when air enters a suitable silica material having a nano-sized pore structure, a thin film having a relatively low dielectric constant ("k") can be prepared. Nanosilica materials have attracted attention because they are similar to the precursors and contain organically substituted silanes, such as using tetraethoxysilane (TAS) / methyltriacetoxysilane (MTAS) -derived silicon polymers as Basic substrate, and is used for spin coating ("SOG") and chemical vapor deposition ("CVD") of silica (SiO2) glass currently used. This material has proven high mechanical strength, as shown by the modulus and distribution 84564 200403764 grabbing data. Mechanical properties can be controlled by inch distribution. Nanoporous 2: Amphoteric films have controllable void sizes, and therefore the resulting films :: mesh: because of their pore size and dielectric constant. In addition to low k, the nanometer is thin: the heat of the degree and mechanical strength is reached. The point contains at least lower than the microelectronic characteristics of the integrated circuit = inch size = inch size-, ', and can be used as a semi-conductive Jinyu library The used crushed stone and tetraethoxylate ceramics) are prepared; the dielectric constant of raw crushed stone can be "adjusted" in the wire circumference; and the nano-porous material can be used in the same way as S.aG. Similar equipment is achieved. Therefore, the high porosity of the same material in the silica material is the same, and the number of packages is lower than that of the porous nano-porous film, and the relative density of the material is changed. Other materials = Including the dimensions that require all pores to have substantially small M characteristics, need = the effect of surface chemistry due to the decrease in strength due to porosity 'and its dielectric constant and environmental stability. Density (or porosity) is the main parameter of the nanometer film that controls the dielectric constant of the material. The property of 'JL can be easily changed on a continuous map, from a maximum air gap of 100% to a porosity of 0%. Dense silica. When the porosity increases, the dielectric constant and mechanical strength increase, but the porosity decreases, etc. This suggests that the density range of nanoporous films should be optimally balanced between the low dielectric constant range and mechanical properties required for the desired application. Nanoporous silica films have been previously manufactured in many ways. For example, nanoporous films have been prepared using a mixture of a solvent and a silica precursor, which is deposited on a suitable substrate. Generally, a precursor such as 84564 200403764 in spin coating form on a glass is added to a substrate and then polymerized in the form of a dielectric thin film including nanopores. When the nanoporous film is formed by, for example, spin coating, the film coating is generally catalyzed by an acidic or alkaline catalyst and water, causing polymerization / gelling ("aging") during the initial heating process. Maximum strength 'is not obtained by selecting the pore size and therefore a low molecular weight pore former is used. U.S. Patent No. 5,895,263 describes heating a composition on a substrate such as a wafer by coating the composition including a decomposable polymer and an organic polysilica (that is, a polymer containing condensation or polymerized silicon). The polysilica is further condensed, and the decomposable polymer is decomposed to form a porous dielectric layer to form a nanoporous silica dielectric film. This method is similar to many previous methods used to form nanoporous films on semiconductors, with the disadvantage that f is heated during the aging or condensation process and the polymer is removed to form a nanoporous film. Moreover, the disadvantage is that the organic polysilica contained in the precursor solution will increase the molecular weight after the preparation of the solution. Therefore, the storage solution is dissolved to increase the viscosity during the storage process. 'JL is thin from the storage solution = Increasing the storage time. The organic aggregation is disturbed by the storage time, cooling storage, and precise adjustment of the parameters, which is achieved during the manufacturing process of the microchip circuit. The condition for the formation of W porous structure depends on the cross-linking temperature (or gelation temperature) of the material. It was found that below ^ = ions such as: the positive positivity of two L7 porous structures in solution rotating in accordance with Ic shore use 'ppb level can not be manufactured. However, the urgent need for… Medium Low Metal Concentration is generally practiced as the metal concentration of spinning on 84564 200403764 4 fluid is below 50 ppb. Therefore, there is a need to develop a low-metal nanoporous silica film that can continuously provide a dielectric constant below 2.5 and a pore size with a diameter below 10 ㈣. It has now been discovered that porous silica networks can be formed at low temperatures in low metal spin formulations by using tritium ions or nucleophiles. The role of osmium ions or nucleophiles is to lower the gelation temperature. Because the hard network can be hardened before the pore former is removed, nanoporous films can be manufactured without the need for undesired experimental ions. [Summary of the Invention] The present invention provides a method for manufacturing a nanoporous silica dielectric thin film, which includes the preparation of a pre-cut polymer, a porogen, and a metal-free ion selected from the group consisting of a scandium compound and a nucleophile. Catalyst composition; (b) coating the substrate with the composition to form a film; (c) cross-linking the composition to produce a gel film, and heating and removing the gel film at temperature and during the effective period Virtually all of this pore former. This month, a composition including a prepolymer, a porogen, and a catalyst selected from the group consisting of radium compounds and nucleophiles is also provided. This method provides a method for reducing the temperature at which a porous silica film is formed. The method includes the steps of adding a europium ion or a nucleophile to a prepolymer and a pore former containing stone. [Embodiment] The following nanoporous silica is prepared. Generally, based on silicon, a dielectric constant or k value of about 3 or a dielectric film can be produced by the method of the present invention. 84564 200403764 ^ film (including nanoporous crushed dielectric thin ^ and It can be prepared from a rhenium compound or a nucleophile without metal ions. It can be used as a general-purpose cutting prepolymer composition. It can also include this type = blending-rhenium solvent and / or other ingredients. Know the method, paint you, = Tian by any technical equipment η μΓ cloth common substrate, such as manufacturing semiconducting bone fan, placed as a substrate for integrated circuit ("IC,"), shape guide: The composition is cross-linked to form a thin film. The film is prepared by heating the gelled film under the same plate to remove all pore-forming agents. The film prepared by the method of the invention has many Youzhi "Advantages, including improved mechanical strength, which can produce films that can withstand the processing steps required for the preparation of semiconductors, industrial equipment, and other devices on substrates, and have a stable dielectric constant. Stable dielectric The properties of the electrical constant can be achieved without the need to form nano-porous lithiac dielectric films. The steps required for the method are beneficially achieved under the surface modification step. In addition, the W stone film produced by the method of the present invention can be sufficiently hydrophobic as initially formed. Furthermore, the method of the present invention is directed to prepolymerization of coating The initial polyt (i.e., gelation or aging) of the composition advantageously requires relatively low temperature. In the method 2 of the present invention, the pore size with a diameter of 2 nanometers and the size distribution are uniform. The obtained porous silica film The dielectric constant is generally about 3 or less, more usually about ⑷.3 to about 3.0 ′ and most usually about h7 to about 2.5. The average pore straightness of the film = usually about 1 brittle to about 30 It is more preferably about 1 nm to about 1 (nm), and is usually about 1 nm to about 5 nm. The pore volume of the film is based on the entire volume of the film, and is generally about 5% to about 80%. It should be understood that nanoporous The term "dielectric thin film" refers to a dielectric thin film prepared by the method of the present invention, 84564 -10- / 64, from an organic or inorganic sloped glass substrate material (for example, any applicable hard-based :). "Aging" refers to the "hardened word" on the substrate after the deposition of a combination of other stone-based expulsion compositions. (Iv) means a left shift of · 0H) group, removal of water, and more stable braking ϋ methodology of the film in subsequent processing of the method of manufacturing the micro-son process. The hardening process is performed after gelling and is generally performed by heating, but any other hardening form known in the art may be used, such as by applying energy in the form of electron beams, ultraviolet radiation, and the like. Dielectric films such as spaced dielectric coatings are prepared from palatable compositions coated on a substrate. The art of coating body dielectric precursor composition is known in the art, and the method includes (but is not limited to) spin coating, dip coating, brush coating with roller coating 2 :, cloth = / or chemical gas deposition. When coating these material types to form a thin dielectric material, the surface of the earth material can be prepared by standard and clean methods according to the conditions of the coating. The coating is processed to achieve the desired type; and 舁: The electro-chemical coating is consistent, and the processing steps are selected to suit the selection of :: flooding and the desired final product. Other details of this method and composition are as follows. The < substrate used in the present invention, which is included in the coating of the nano-cut stone film of the present invention, is generally suitable for manufacturing integrated circuit-cut wafers, and the basic material for forming the nano-porous cut stone film is coated by a general method. Before spraying on the substrate = (but not limited to) spin coating, dip coating, brush coating, roll coating, and / or coating the base material to form a nanoporous stone sapphire film, the surface of the substrate may be based on the situation Prepared by standard, known cleaning methods. 84564 • 11-200403764 The weekly substrates of the present invention include semiconductor substrates such as gallium arsenide ("GaAs"), silicon, and silicon-containing compositions such as crystalline silicon, polysilicon, amorphous silicon, and oriented silicon , And silicon dioxide ("Si02 ,,") and mixtures thereof. The substrate < is a surface-selected pattern that produces lines, such as metal, oxide, lice or oxynitride lines. It is formed by the conventional lithographic etching technique. A suitable material for the line includes hafnium oxide

鈦、氮化鈕、I呂、鋁合金、銅、銅合金、鈀、鎢及氧基氮 化石夕。製造此等線條所用之金屬標的物係教示於共同受讓 之美國專利第 5,780,755 ; 6,23M94 ; 6,331,233b1m,348、,i39bi 中 :且由H〇neywell國際公司銷售。此等線條形成積體電路之 導體或絕緣體。此一般係以約2〇微米或更短之距離,較好 為1微米或更近’且最好約0_05至約1微米之距離彼此緊密的 分離。適用基材表面之其他選狀特性包含氧化物層,如 由使矽晶圓在空氣中加熱形成之氧化物層,或更好為藉由 =技藝中已知之材料(例如電漿提昇之四乙氧基我氧化物 (PETEOS ) ' % 提昇之碎垸氧化物(“p㈣燒”)及其結合 =)化學条氣沉積形成之Si〇2氧化物層,以及一層或多層先 酌形成之奈米石夕石介電質薄膜。 、、本I明4夕孔性秒石薄膜可經塗佈,以覆蓋及/或平鋪 該選用之電子表面特徵之間,例如先前已經形成之基材 除(兒路7L件及/或導電路徑。該選用之基材特性亦可以 少-額外之層塗佈於本發明奈米多孔㈣石薄膜之上, 此低介電質薄膜可使所得積體電路之—或多層或許多電 及/或%子功㈣層絕緣。因此,本發明之基材可視情況包 84564 -12- 200403764 在製造多層或多組件積體電路之過程中,在本發明奈米多 孔性矽石薄膜之上或與之相鄰形成之矽材料。依另一選擇 ,帶有本發明奈米多孔性矽石薄膜之基材可以技藝中已知 之非多孔性絕緣層,例如玻璃覆蓋層進一步覆蓋。 用於形成本發明奈米多孔性薄膜之可交聯組合物包含一 種或多種可立即縮合之含矽預聚物。其應具有至少二個可 水解之反應性基。該反應性基包含烷氧基(RO)、乙醯氧基 (AcO)、等。在不受如何達成本發明之方法及組合物之理論 及假設之限制下,相信水會使矽單體上之反應基水解,形 成Si-OH基(矽烷醇)。後者會與其他矽烷醇或與其他反應性 基進行縮合反應,如下式之說明:Titanium, nitride buttons, aluminum alloys, copper, copper alloys, palladium, tungsten, and oxynitride. The metal objects used to make these lines are taught in commonly assigned U.S. Patent Nos. 5,780,755; 6,23M94; 6,331,233b1m, 348, and i39bi: and are sold by Honelwell International. These lines form a conductor or insulator of the integrated circuit. This is generally closely separated from each other at a distance of about 20 micrometers or less, preferably 1 micrometer or less', and most preferably about 0_05 to about 1 micrometer. Other selection characteristics suitable for the surface of the substrate include an oxide layer, such as an oxide layer formed by heating a silicon wafer in the air, or more preferably a material known in the art (for example, a plasma booster) Oxygen oxide (PETEOS) '% elevated fragmented plutonium oxide ("p㈣fired") and its combination =) Si02 oxide layer formed by chemical stripe deposition, and one or more nanometers formed as appropriate Shi Xishi dielectric thin film. The porous second stone film can be coated to cover and / or tile between the selected electronic surface features, such as previously formed substrates (7L pieces and / or conductive) The characteristics of the selected substrate can also be reduced-additional layers are coated on the nanoporous vermiculite film of the present invention. This low-dielectric film can make the resulting integrated circuit-or multiple layers or many electrical and / Or the% sub-conductor layer insulation. Therefore, the substrate of the present invention may be packaged according to circumstances 84564-12-200403764. In the process of manufacturing a multilayer or multi-component integrated circuit, on the nanoporous silica film of the present invention or with The silicon material formed next to each other. According to another option, the substrate with the nanoporous silica film of the present invention may be further covered with a non-porous insulating layer known in the art, such as a glass cover layer. The crosslinkable composition of a nanoporous film comprises one or more silicon-containing prepolymers that can be condensed immediately. It should have at least two hydrolyzable reactive groups. The reactive groups include alkoxy (RO), Acetyloxy (AcO), etc. Within the limits of the theory and assumptions of the method and composition of the invention, He Da believes that water will hydrolyze the reactive groups on the silicon monomer to form Si-OH groups (silanol). The latter will react with other silanols or with other The basic group undergoes a condensation reaction, which is described by the following formula:

Si-OH + HO-Si -^Si-0-Si+ H20 Si-OH + RO-Si ->Si-0-Si+ ROH Si-OH + AcO-Si Si-0-Si+ AcOH Si-OAc + AcO-Si ~> Si-O-Si A〇2〇 R =燒基或芳基 Ac=醯基或(CH3CO) 此等縮合反應會形成含矽之聚合物。本發明之一具體例 中,預聚物包含以式I表示之化合物或化合物之任何結合: Rx - Si - Ly (式 I) 其中x為0至約2之整數,且y為4-x(約2至約4之整數), R係獨立為烷基、芳基、氩、伸烷基、伸芳基及/或此等之 結合, L係獨立選自負電性基,例如烷氧基、羧基、胺基、醯胺 -13- 84564 200403764 基、鹵化物、異氰酸醋基、及/或此等之結合。 最有用之預聚物為由式I提供者,其中X約為〇至約2,y約 為2至約4,R為烷基或芳基或Η,且L為負電性基,且其中 Si-L键之水解速率大於Si-〇CH2CH3键之水解速率。因此,針 對下列以⑷及(b)表示之反應:Si-OH + HO-Si-^ Si-0-Si + H20 Si-OH + RO-Si-> Si-0-Si + ROH Si-OH + AcO-Si Si-0-Si + AcOH Si-OAc + AcO- Si ~> Si-O-Si A〇2〇R = alkyl or aryl Ac = fluorenyl or (CH3CO) These condensation reactions will form silicon-containing polymers. In a specific example of the present invention, the prepolymer includes a compound represented by Formula I or any combination of compounds: Rx-Si-Ly (Formula I) where x is an integer from 0 to about 2, and y is 4-x ( An integer from about 2 to about 4), R is independently selected from alkyl, aryl, argon, alkylene, aryl, and / or combinations thereof, and L is independently selected from negatively charged groups such as alkoxy, Carboxyl, amine, amidine-13- 84564 200403764, halide, isocyanate, and / or combinations thereof. The most useful prepolymers are provided by Formula I, where X is from about 0 to about 2, y is from about 2 to about 4, R is an alkyl or aryl or fluorene, and L is a negatively charged group, and where Si The hydrolysis rate of the -L bond is greater than the hydrolysis rate of the Si-OCH2CH3 bond. Therefore, the following reactions are represented by ⑷ and (b):

⑻ Si-L + H2〇Si-OH + HL (b) Si_OCH2CH3+ H20 Si-〇H+ HOCH2CH3 ⑻之速率大於(b)之速率。 式I適用化合物之實例包含(但不限):⑻ Si-L + H2〇Si-OH + HL (b) Si_OCH2CH3 + H20 Si-OH + HOCH2CH3 The rate of ⑻ is greater than the rate of (b). Examples of suitable compounds of formula I include, but are not limited to:

Si(OCH2CF3)4 肆(2,2,2-三氟乙氧基)矽烷,Si (OCH2CF3) 4 (2,2,2-trifluoroethoxy) silane,

Si(〇COCF3)4 肆(三氟乙醯氧基)矽烷*,Si (〇COCF3) 4 (trifluoroacetoxy) silane *,

Si(〇CN)4 四異氰酸酯基矽烷, CH3Si(〇CH2CF3)3參(2,2>三氟乙氧基)甲基矽烷, CH3Si(OCOCF3)3參(三氟乙醯氧基)甲基矽烷*, CH3Si(〇CN)3 甲基三異氰酸酯基矽烷, [*此等在暴露於水時會產生酸觸媒] 及/或上述任何之結合。 依本發明另一具體例,該組合物包含以水解及縮合反應 ,兔 約為150至約300,000 amu,或通常約為150至約10,000 amu。 依本發明另一具體例,本發明使用之含矽預聚物包含有 機矽烷,例如包含下式II之烷氧基矽烷: -R R——si——R R- 11 -14- 84564 200403764 視情況,式II為烷基矽烷,其中至少2個R基係獨立為C14 燒氧基,且其於(若存在)係獨立選自由氫、烷基、苯基、 卣素、經取代之苯基組成之群組。針對本發明之目的,垸 氧基一詞包含可輕易的在室溫下經水解自矽斷鏈之任何其 他有機基。R 基可為 ethylene glycoxy 或 propylene glyc〇xy、等, 但f好全部4個R基均為甲氧基、乙氧基、丙氧基或丁氧基 最佳之烷氧基矽烷包含四乙氧基矽烷(丁E〇s)及四甲氧基 矽烷。Si (〇CN) 4 tetraisocyanate silane, CH3Si (〇CH2CF3) 3 ginseng (2,2 > trifluoroethoxy) methyl silane, CH3Si (OCOCF3) 3 ginspan (trifluoroacetoxy) methyl silane *, CH3Si (〇CN) 3 methyltriisocyanate silane, [* This will generate an acid catalyst when exposed to water] and / or any combination of the above. According to another embodiment of the present invention, the composition comprises a hydrolysis and condensation reaction, the rabbit is about 150 to about 300,000 amu, or usually about 150 to about 10,000 amu. According to another specific example of the present invention, the silicon-containing prepolymer used in the present invention includes an organic silane, for example, an alkoxysilane containing the following formula II: -RR——si——R R- 11 -14- 84564 200403764 as appropriate , Formula II is an alkylsilane, wherein at least two R groups are independently C14 alkoxy, and if present, they are independently selected from the group consisting of hydrogen, alkyl, phenyl, halogen, and substituted phenyl Group. For the purpose of the present invention, the term fluorenyl includes any other organic group that can be easily hydrolyzed from silicon chain scission at room temperature. The R group can be ethylene glycoxy or propylene glycoxy, etc., but all 4 R groups are methoxy, ethoxy, propoxy or butoxy. The best alkoxy silanes include tetraethoxy Silane (butanes) and tetramethoxysilane.

依另一選擇,例如預聚物亦可為式^所述之烷基烷氧基 矽烷,然而至少2個R基係獨立為Cm烷基烷氧基,其中之烷 基基團gcM烷基,而烷氧基基團為Ci0烷氧基,或醚-烷氧 基,且其餘(若存在)則獨立選自由氫、烷基、苯基、鹵素According to another option, for example, the prepolymer may also be an alkylalkoxysilane described in Formula ^, but at least two R groups are independently Cm alkylalkoxy groups, wherein the alkyl group is gcM alkyl, The alkoxy group is Ci0 alkoxy, or ether-alkoxy, and the rest (if present) are independently selected from hydrogen, alkyl, phenyl, and halogen

、經取代之苯基組成之群組。依其一較佳具體例,各 甲氧基、乙氧基或丙氧基。依另一較佳具體例,至少二 基為烷基烷氧基,其中之烷基基團為Cm烷基,且烷氧基』 團為烷氧基。依又另一蒸氣相前驅物之較佳具體例,^ 少二R基為式(CW充氧基垸氧基(其中福2至6)。 較佳之含矽預聚物包含例如烷氧基矽烷之任一種或結^ 物-—如四^ 、u異丙氧基矽烷、A group of substituted phenyl groups. According to a preferred embodiment, each of them is methoxy, ethoxy or propoxy. According to another preferred embodiment, at least the diyl group is an alkylalkoxy group, wherein the alkyl group is a Cm alkyl group, and the alkoxy group is an alkoxy group. According to yet another preferred specific example of the precursor of the vapor phase, the ^ -lower R group is of the formula (CW oxygenated fluorenyloxy group (wherein 2 to 6). Preferred silicon-containing prepolymers include, for example, alkoxysilanes Any one or structure ^-such as tetra ^, u isopropoxysilane,

四(甲氧基乙氧基)硬垸、四(甲氧基乙氧基乙氧基㈣燒,》 均具有四個可水解接著縮合製造碎石之基,燒基燒氧基巧 、甲基一乙氧基矽烷,芳基烷氧基矽烷如苯基三乙氧j 夕:^及則驅物如二乙氧基石夕貌,其會對薄膜產生紐官能伯 。本發明最有用者為肆(甲氧基乙氧基乙氧基㈣燒、肆U 84564 -15- 200403764 乳基^氧基)石夕燒、肆(丁氧基乙氧基乙氧基)矽烷、肆(2-乙 氧土)夕心、肆(甲氧基乙氧基)碎燒、及肆(甲氧基丙氧 基)碎燒。 /依本發明又另一具體例,上述烷氧基矽烷化合物可全部 或卩刀以具有乙醯氧基及/或以自素為主之離去基取代。例 /、水物可為乙醯氧基(CH3_c〇_〇_),如乙醯氧基-石夕燒化 口物及/或齒化之化合物,例如齒化之矽烷化合物及/或其 結合物。針對_化之預聚物,自素為例如a、Br、τ,且依 特走目的可視情況含F。較佳之乙醯氧基衍生之預聚物包含 例如肆乙§1氧基碎燒、甲基三乙酿氧基碎垸及/或其結合。 八依本發明之一特殊具體例,含矽之預聚物包含單體或聚 合物可驅物,例如乙醯氧基矽烷、乙氧基矽烷、甲氧基矽 燒及/或其結合。 /衣本發明更佳之具體例,切之預聚物包含四乙氧基石夕 烷Cl 土約C6烷基或芳基-三乙醯氧基矽烷及其結合。尤其 ’如以下所列,三乙酿氧基找為甲基三乙醯氧基石夕燒。 含石夕之預聚物在全部組合物中之含量約為1〇奶%至約8〇 wt%,較好在全部組合物中之含量為約2〇奶%至約6〇斯%。 〜針對非微電子之用途,鑌或親核性觸媒可含金屬離子。 實例包含氫氧化鈉、硫酸鈉、氫氧化鉀、氫氧化鋰、及含 鍺之觸媒。 針對微電子應用’較好’組合物再含至少一種為鑌化合 物或親核物之無金屬離子觸媒。觸媒可為例如銨化合物、 胺、鱗化合物或膦化合物。纟實例包含四有機按化合物及 -16- 84564 200403764 四有機鳞化合物,包含四甲基銨乙酸鹽、四甲基銨氫氧化 物、四丁基銨乙酸鹽、三苯基胺、三辛基胺、三十二烷基 胺、二乙醇胺、四甲基鳞乙酸鹽、四甲基鱗氫氧化物、三 苯基膦、三甲基膦、三辛基膦及其結合物。該組合物可包 括非金屬、親核性添加劑,其可加速組合物之交聯。此等 包吕一甲基颯、—甲基甲胺、$甲基構三酸胺丁)、 胺及其結合物。觸媒在全部組合物中之含量較好約i ppm ㈣至約誦醉,且其在全部組合物中之含量較好為⑽ ppm 至約 200 ppm。 該組合物再含至少-種成孔劑。成孔劑可為化合物或寡 聚物或聚合物’且係經選擇使得當被移除(例如藉由加熱: 時’可屋生具有奈米規格多孔性結構之Θ石介電質薄膜。 :由移除成孔劑產生之孔隙之尺寸與選用之成孔劑成分之 有效互體直徑成正比。任何特殊孔隙尺寸(亦即直徑 ^係藉由使用薄膜之半導體裝置之尺寸定義。另外 附:太小造成產生之孔隙阻塞,例如該小直徑結構中之 =:導致:成非多孔性(密實)薄膜。再者,提供之薄 =隙分布中所有孔隙之直徑變化應為最小。較好,成 樣品中具有實質均勻分子量及分子: 化4辟: /或分子尺寸之統計上分布或範圍之 明方二、:子重量分布中之任何明顯變化可使以本發 薄膜:之孔隙、直徑實質均勻的分布。若產生 丹腺具有廣X爻孔隙尺寸分右 大孔隙(亦即氣泡)之形成增加 的會使-或多個 而對製造可靠半導體裝置Tetrakis (methoxyethoxy) hard fluorene, tetrakis (methoxyethoxyethoxy), sintered, have four groups that can be hydrolyzed and then condensed to produce crushed stone. Monoethoxysilane, arylalkoxysilane, such as phenyltriethoxy, and the precursors such as diethoxylate, which will produce a new functional group on the film. The most useful of the present invention is (Methoxyethoxyethoxylate, U 84564 -15- 200403764 lactyl ^ oxy) Shi Xiyan, Iso (butoxyethoxyethoxy) silane, Iso (2-ethoxy (Earth) Xixin, mash (methoxyethoxy), and mash (methoxypropoxy). / According to yet another specific example of the present invention, the above alkoxysilane compounds may be all or 卩The knife is substituted with a leaving group having ethoxyl and / or self-priming. For example, the water may be ethoxyl (CH3_c〇_〇_), such as ethoxyl-shixi calcination Mouth and / or dentin compounds, such as dentin silane compounds and / or combinations thereof. For prepolymers, the primes are, for example, a, Br, τ, and may contain F depending on the purpose. .Better Oxygen-derived prepolymers include, for example, ethylene oxide sintering, methyl triethyl alcohol oxyfluorene, and / or combinations thereof. Eighth, according to a specific embodiment of the present invention, the silicon-containing prepolymer includes Monomer or polymer catalysable substance, such as ethoxysilane, ethoxysilane, methoxysilane and / or a combination thereof. / In a more preferred embodiment of the present invention, the cut prepolymer contains tetraethoxy Keystone oxane Cl soil C6 alkyl or aryl-triethoxysilane and its combination. In particular, as listed below, triethyl alkoxy is found as methyltriethyloxy oxane. The content of the prepolymer in the entire composition is about 10% to about 80% by weight, and preferably the content of the prepolymer in the total composition is about 20% to about 60% by weight. For electronic applications, thallium or nucleophilic catalysts can contain metal ions. Examples include sodium hydroxide, sodium sulfate, potassium hydroxide, lithium hydroxide, and germanium-containing catalysts. 'Better' compositions for microelectronic applications It further contains at least one metal ion-free catalyst which is a europium compound or a nucleophile. The catalyst may be, for example, an ammonium compound, an amine, or a scale compound Phosphine compounds. Examples include tetraorganic compounds and -16-84564 200403764 tetraorganic scale compounds, including tetramethylammonium acetate, tetramethylammonium hydroxide, tetrabutylammonium acetate, triphenylamine, Octylamine, dodecylamine, diethanolamine, tetramethylphosphonium acetate, tetramethylphosphonium hydroxide, triphenylphosphine, trimethylphosphine, trioctylphosphine, and combinations thereof. The combination The compounds may include non-metallic, nucleophilic additives, which can accelerate the cross-linking of the composition. These include monomethylsulfonium, -methylmethylamine, methyltriamidine, amines, and combinations thereof. The content of the catalyst in the entire composition is preferably about i ppm to about 200 ppm, and the content of the catalyst in the entire composition is preferably from about ppm to about 200 ppm. The composition further contains at least one pore former. Pore formers can be compounds or oligomers or polymers 'and are selected such that when removed, for example, by heating:' Keho can produce a Θ stone dielectric film with a nano-sized porous structure: The size of the pores resulting from the removal of the pore-forming agent is directly proportional to the effective interbody diameter of the pore-forming agent component selected. Any special pore size (i.e., diameter ^ is defined by the size of the semiconductor device using the thin film. In addition: Poor blockage of pores caused by too small, for example == in this small diameter structure leads to: non-porous (compact) film. Furthermore, the thinness provided = the diameter change of all pores in the gap distribution should be minimal. Better, The finished sample has a substantially uniform molecular weight and molecules: Chemical formula: / or the statistical distribution or range of molecular size. Second, any significant change in the sub-weight distribution can make the thin film of the hair: Uniform distribution. If the Dan gland has a wide X 爻 pore size, the formation of right large pores (that is, air bubbles) will increase-or more, which will be useful for manufacturing reliable semiconductor devices.

84564 -17- 200403764 產生困擾。 再者,成孔劑應具有在不干擾薄膜形成下自薄膜 ,擇性移除之分子量及結構。此係以半導體裝置之性質而 足二其—般具有上限之加工溫度。大體而言,成孔劑應可 在溫度低於例如約450t下自新形成之薄膜移除。特殊具體 例中’依所需之後薄膜形成製造方法及材料而定,成孔劑 係選擇在30秒至約60分鐘内,可在約丨冗^至約45〇。〇之溫^ 下輕易移P佘者。&孔劑之移除可藉由纟大氣壓下或之上或 在j空中將薄膜加熱,或使薄膜暴露於輻射下或二者引發。 、四付合上述特性之成孔劑包含其沸點、昇華溫度及/或分解 度(大氣壓下)約為15〇艽至約45〇t之化合物及聚合物。另 外本發明適用之成孔⑳包含分子量為例如約1〇〇至約5〇,〇〇〇 amu,且更好約為1〇〇至約3,〇〇〇amu者。 , 本發明之方法及組合物中適用之成孔劑包含聚合物,且 較好含有一個或多個反應性基如羥基或胺基者。此等一般 參數中,本發明之組合物及方法中適用之聚合物成孔劑為 例如聚ί哀氧烷、聚環氧烷之單醚、聚環氧烷之二醚、聚環 虱:兄《雙酯、脂系聚酯、丙烯酸系聚合物、乙縮醛聚合物 水(己内酉曰)、聚(戊内酯)、聚(甲基丙烯酸甲酯)、聚(乙烯 基丁醛)及/或其結合物。當成孔劑為聚環氧烷單醚時,其 一特殊具體例為在氧原丨及口至約Q燒基酸基團間之〇1至 、·.、 6'兀土鏈且其中之燒基鏈為飽和或不飽和,例如聚乙 _醇單甲基鍵 ' 聚乙二醇二甲基酸、或聚丙二醇單Τ基酸。 其他通用之成孔劑係敘述於與該申請案同一天申請之共 84564 -18- 200403764 同又讓之專利申請案編號__中,其係不與含矽之預聚 物=結之成孔劑,且包含聚(伸烷基)二醚、聚(伸芳基)二醚 取=(環二醇)二醚、冠狀醚、聚己内酯、全部封端保護之 聚環氧烷,完全封端保護之聚伸芳基氧化物、pdyn〇rbene、 及其結合物。不會與含矽之預聚物鍵結之較佳成孔劑包含 水(乙一醇)一甲基醚、聚(乙二醇)雙(羧基甲基)醚、聚(乙二 醇)二苯甲酸酯、聚(乙二醇)二甘油醚、聚(丙二醇)二苯甲 酸酉曰、聚(丙.二醇)二甘油醚、聚(丙二醇)二甲基醚、15_冠 狀醚_5、18-冠狀醚_6、二苯并-18_冠狀醚_6、二環己基_18_冠 狀醚-6、二苯并_15_冠狀醚·5、及其結合物。 為不文如何操作本發明之任何理論及假設之限制,相信 “可輕易自薄膜移除,,之成孔劑係在下列狀沉之一或結合 下·⑴成孔劑係在加熱步驟下物理蒸發,⑺將成孔劑劣化 成更可揮發之分子片段,(3)使成孔 劑及含Si之成分間之鍵 斷裂,接著使成孔劑自薄膜蒸發,或模式μ3之任何結合。 成孔劑經加熱直到移除實質比例之成孔劑為止,例如移除 至少約50 wt%或更多之成孔劑。尤其,某些具體例中,依 選用之成孔劑及薄膜材料,至少移除約75斯%或更多之成 孔劑。 因此,“實質,,一詞意指(僅為列舉用)自塗佈之薄膜移除 約5〇%至約75%或更多之原有成孔劑。 全邵組合物中之成孔劑含量較好約為1至約5〇或更多 。更好組合物中之成孔劑含量約為2至約20 Wt%。 全部組合物可在視情況下包含溶劑組合物。本文中參考 84564 -19 - 200403764 之‘‘落劑”應包含單一溶劑,極性或非極性及/或形成選自可 使全邵組合物成分溶解之溶劑系統之可相容溶劑之結合。 落劑可視情況包含於組合物中以降低其黏度,且促進其以 技蟄中之標準方法(例如旋轉塗佈、噴塗、浸潰塗佈、滾塗 等)均勻的塗佈於基材上。 為協助移除溶劑,溶劑為相對於任何選用之成孔劑及其 他前驅物成分之沸點具有相對低沸點者。例如,本發明之 方法中所用之溶劑之沸點在約50至約25(rc之間,使溶劑可 自塗佈之薄膜療發’且離開前驅物組合物之活化部分。為 符合各種安全及環境之需求,溶劑較好具有高閃蒸點(通常 超過40。〇及相對低度之毒性。適用之溶劑包含例如烴以及 具有官能基c_o_c(^)、-cao(醋)、_co·(酮)、_〇H(醇)及(ον-(醯胺 ) 之溶劑 ,及含許多此等官能基之溶劑及其結合。 為不受限制,組合物之溶劑包含二正丁基醚、丙酮、3_ 戊酮、2-庚酮、乙酸乙酯、乙酸正丙酯、乙酸正丁酯、乳 酸乙酯、6醇、2-丙醇、二甲基乙醯胺、丙二醇甲基醚乙 酸酉旨及/或其結合物。較好溶射與切之預聚物成分反應。 洛劑成分之含量較好為全部組合物之約1〇斯%至約% 。更好為約20 wt%至約75奶%,且最好為約2〇感至 約 60 wt% 、。所用溶劑之百分比愈大’則所得薄膜愈厚。所用成孔劑 之百分比愈大,則所得孔隙度愈多。 依本發明另一具體例,組合物可包括水(水或水蒸氣)。 例如,可將全邵組合物塗佈於基材上,接著在標準溫度及 標準壓力下使其暴料含水蒸氣之周圍氣體中。視情況,84564 -17- 200403764 caused trouble. Furthermore, the porogen should have a molecular weight and structure that is selectively removed from the film without disturbing the film formation. This is due to the nature of the semiconductor device, which generally has an upper processing temperature. In general, the pore former should be removable from the newly formed film at a temperature below, for example, about 450t. In the specific embodiment, depending on the required method and material for forming a thin film afterwards, the pore-forming agent is selected within 30 seconds to about 60 minutes, and can be redundant to about 45 °. 〇 之 温 ^ Move P 佘 easily. & Removal of porosity can be initiated by heating the film at or above atmospheric pressure or in the air, or exposing the film to radiation or both. The four-hole-forming pore-forming agent includes compounds and polymers having a boiling point, sublimation temperature, and / or a degree of decomposition (under atmospheric pressure) of about 150 ° to about 450 °. In addition, the pore-forming hydrazones to which the present invention is applicable include those having a molecular weight of, for example, about 1,000 to about 50,000 amu, and more preferably about 100 to about 3,000 amu. The pore formers suitable for use in the methods and compositions of the present invention include polymers and preferably contain one or more reactive groups such as hydroxyl or amine groups. Among these general parameters, the polymer pore-forming agents suitable for use in the compositions and methods of the present invention are, for example, polyoxyalkylene, monoethers of polyalkylene oxides, diethers of polyalkylene oxides, polycyclic lice: brothers "Diester, fatty polyester, acrylic polymer, acetal polymer water (caprolactone), poly (valerolactone), poly (methyl methacrylate), poly (vinyl butyral) And / or a combination thereof. When the pore-forming agent is a polyalkylene oxide monoether, a special specific example thereof is between 0, 1, ..., and 6 'wutu chain between the oxygen source and the mouth to about Q alkyl groups, and the burning thereof is The base chain is saturated or unsaturated, such as a polyethylene glycol monomethyl bond, a polyethylene glycol dimethyl acid, or a polypropylene glycol mono Tyl acid. Other common pore-forming agents are described in the same patent application number __, which was filed on the same day as the application. It is not pore-forming with the silicon-containing prepolymer = Agent, and contains poly (alkylene) diether, poly (arylene) diether = (cyclodiol) diether, crown ether, polycaprolactone, all capped polyalkylene oxide, completely End-protected polyarylene oxide, pdynorbene, and combinations thereof. Preferred pore formers that do not bind to silicon-containing prepolymers include water (ethylene glycol) monomethyl ether, poly (ethylene glycol) bis (carboxymethyl) ether, and poly (ethylene glycol) diphenyl. Formate, poly (ethylene glycol) diglyceryl ether, poly (propylene glycol) dibenzoate, poly (propylene.diol) diglyceryl ether, poly (propylene glycol) dimethyl ether, 15_crown ether_5 , 18-crown ether_6, dibenzo-18_crown ether_6, dicyclohexyl_18_crown ether-6, dibenzo_15_crown ether · 5, and combinations thereof. In order not to limit any theory or hypothesis of how to operate the present invention, it is believed that "the porogen can be easily removed from the film. The porogen is one of the following or a combination of the following: The porogen is physically under the heating step. Evaporation causes the porogen to degrade into more volatile molecular fragments, (3) breaks the bond between the porogen and the Si-containing component, and then causes the porogen to evaporate from the film, or any combination of modes μ3. The porogen is heated until a substantial proportion of the porogen is removed, for example, at least about 50 wt% or more of the porogen is removed. In particular, in some specific examples, depending on the porogen and film material selected, at least Removes about 75 s% or more of the porogen. Therefore, "essentially," the term means (for example only) removing about 50% to about 75% or more of the original There are porogens. The porogen content in the whole Shao composition is preferably from about 1 to about 50 or more. More preferred compositions have a porogen content of from about 2 to about 20 Wt%. All compositions may optionally include a solvent composition. The "dropping agents" referred to herein as 84564-19-200403764 should include a single solvent, polar or non-polar, and / or a combination of compatible solvents selected from a solvent system that can dissolve the ingredients of the whole composition. It may be included in the composition to reduce its viscosity, and promote its uniform coating on the substrate by standard methods (such as spin coating, spray coating, dip coating, roll coating, etc.). Remove the solvent. The solvent has a relatively low boiling point relative to the boiling point of any selected pore former and other precursor components. For example, the solvent used in the method of the present invention has a boiling point between about 50 and about 25 (rc, Allow the solvent to heal from the coated film and leave the activated part of the precursor composition. In order to meet various safety and environmental requirements, the solvent preferably has a high flash point (usually more than 40.0 and relatively low toxicity) Suitable solvents include, for example, hydrocarbons and solvents having functional groups c_o_c (^), -cao (vinegar), _co · (ketone), _〇H (alcohol), and (ον- (fluoramine)), and many Solvents for functional groups and combinations thereof. For no limitation, the solvent of the composition includes di-n-butyl ether, acetone, 3-pentanone, 2-heptanone, ethyl acetate, n-propyl acetate, n-butyl acetate, ethyl lactate, 6 alcohol, 2- Propanol, dimethylacetamide, propylene glycol methyl ether acetate, and / or combinations thereof. It is better to react with the cut prepolymer component by spraying. The content of the lotion component is preferably about 1 of the total composition. 0% to about%. More preferably about 20% to about 75% by weight, and most preferably about 20% to about 60% by weight. The larger the percentage of solvent used, the thicker the resulting film. The larger the percentage of porogen, the more porosity is obtained. According to another embodiment of the present invention, the composition may include water (water or water vapor). For example, the whole Shao composition may be coated on a substrate, and then Under standard temperature and pressure, it will expose the material to the surrounding gas containing water vapor.

84564 -20- 200403764 孩組合物係在塗佈於基材之前製備,使其包含適合起始前 驅物老化之比例之水,但其比例又不會造成前驅物組合物 塗佈於所需基材之前老化或膠凝。經由實例,當水混合於 前驅物組合物中時,其在包括水之組合物中之比例係依含 矽預聚物中水與Si原子之莫耳比約為01·〗至約5〇:1存在。更 好約為0·1··1至約1〇:1,且最好約為〇·5:1至約15:1。 熱習本技藝者應了解交聯且自奈多孔性介電質薄膜移除 成孔劑之特定溫度範圍係依選用之材料、基材及所需之奈 米規格孔隙結構而定,且可由此等參數之規律性操作測定 通系,絰塗佈之基材係經處理如加熱,使組合物在基材 上交聯,產生膠凝之薄膜。 交聯可在步驟⑷中介由使薄膜在約100t至約25(rc之溫度 :加熱約30秒至約10分鐘之時間,使薄膜膠凝。熟習之技 藝者亦應了解可視情況使用任何額外技藝中已知之硬化方 法’包含依據技藝中已知之方法,藉由使薄膜暴露於電子 束能、紫外線能量、微波能等中施加足夠之能量,使薄膜 硬化。 -旦薄膜老化’亦即充分的縮合成固態或實質之固態, 則可移除成孔劑。後者應足夠的不揮發,以致於在薄ς固 化之前不會自薄膜蒸發。成孔劑係在步驟⑷中藉由在溫度 約150C至約45(TC下,較好在約15〇t至約赋下將膠凝之薄 膜加熱約3G秒中至約1小時移除。本發明重要之特點為較好 步驟⑷之膠凝係在溫度不低於步驟⑼之加熱溫度下進行。 用途 84564 -21 - 200403764 本物亦可包括額外之成分,如黏著促進劑、抗發泡 剑、清春劑、火焰延遲劑、顏料、可塑劑、安定 活性劑。本組合物可用於 ";1 η私于芡應用,如熱絕緣、封 陶资複合材之基質材料、輕重量複合材、隔 曰材、抗腐敍塗層、陶资粉末之結合劑及火培延遲塗异。 ^组合物對於微電子應用中作為微晶片、微晶片模組、 積層電路板或印刷佈線板中之介電質基材材料特別有用。 本組合物亦可用作蝕刻終止劑或硬質光罩。 本薄膜可藉由溶液技術形成,如噴塗'滾塗、浸塗、旋 轉塗佈、流動靠錢鑄及化學蒸氣沉積。針對化學蒸氣 沉積(CVD) ’係將組合物置於CVD裝置中,經蒸發且導入含 欲塗佈基材之室中。蒸發可藉由使組合物在其蒸發點之上 加熱、藉由真空或以上之結合達成。通常,蒸發係在大氣 壓下,驚赋之溫度下達成,或在真空中較低溫(接近室 溫)下達成。 目前有三種型態之CVD:大氣壓㈣(ApcvD)、低壓⑽ (LPCVD)、及電漿提昇之CVD(pECVD)。此等方法之各種均有 優缺點° AP(:VI^置在溫度約為下依質量傳輸限制之 反應杈式操作。依質量傳輸限制沉積,沉積室之溫度控制 比其他方法較不嚴格,因為質量傳輸製程與溫度之關聯性 低。至於反應物達到之速率係與其在整體氣體中之濃度直 接相關,使與晶圓相鄰之整體氣體中之反應濃度維持均勻 相*重要。因此,為確保晶圓上之薄膜厚度均勻,因此在 質量傳輸限制區中操作之反應器需經設計,使所有晶圓之 84564 -22- 200403764 表面均塗佈相等流量之反應物。最廣用之APCVD反應器設 計係藉由水平配置晶圓,且在氣體流下移除,提供均勻之 反應物供給。 相對於APCVD反應器,LPCVD反應器係依反應速率限制 模式操作。依在反應速率限制條件下操作之方法,製程之 溫度為重要之參數。為使全部反應器維持均勻之沉積,因 此反應器溫度在全部反應器中及所有晶圓表面均需均勻。 在反應速率限制之條件下,沉積之物種到達表面之速率並 不如定溫重要。因此,LPCVD反應器並不需設計以供給不 改變之反應物流至晶圓表面之所有位置。 在LPCVD反應器之低壓下,例如在中度真空(30-250 Pa或 0.25至2.0torr)及高溫(550-600°C)下操作,沉積物種之擴散性會 以超過大氣壓下之擴散性約1000之因子增加。增加之擴散 性係藉由反應物須擴散之距離隨著低於壓力之平方根增加 之事實部分補償。實際之作用為反應物傳輸至基材表面且 副產物離開基材表面之增加大小超過一級。 LPCVD反應器係一二主要結構設計:⑻水平管反應器; 及(b)垂直管等溫反應器。水平管狀、熱壁反應器為VLSI製 程中最廣用之反應器。其係用於使多-Si、氮化矽及未摻雜 與摻雜之Si〇2膜沉積。發現如此廣泛的應用係因為其優異 之經濟性、產量、均勻性及可使用大直徑(例如150毫米)晶 圓之能力。 垂直流等溫LPCVD反應器尚可用於分布氣體飼入技術, 使各晶圓均可接收到等量供給之新鮮反應物。晶圓可再度 84564 -23 - 200403764 併排堆疊,但係置於打洞之石英籠中。該籠係置於長的、 打洞之石英反應氣體射出管之下,且對各反應氣體均有一 管。氣體由射出管垂直流經籠之孔定,通過晶圓,與晶圓 表面平行且進入籠下方之排氣狹長口。使用籠孔洞之大小 、數目及位置控制到達晶圓表面之反應氣體流動。藉由使 籠孔洞設計適度之最佳化,可由垂直相鄰之射出管對各晶 圓供給等量之新鮮反應物。因此,該設計可避免終端飼入 管反應氣之晶圓對晶圓之反應物消耗作用,不需溫度下降 ,產生高均勻之沉積,且據稱可達到低的顆粒污染。 第三種主要之CVD沉積法為PECVD。該方法不僅以壓力區 分類,而且亦以其能量之輸入分法分類。除主要以熱能起 始且維持化學反應外,PECVD使用rf-引發之流動排放,將 能量傳入反應物氣體,使基材之溫度維持在低於APCVD或 LPCVD製程之溫度。使基材溫度下降為PECVD之主要優點, 可使沉積在基材上之薄膜不具有足夠之熱安定性,以接受 其他方法之塗層。PECVD亦可使沉積速率提昇至優於使用 熱反應達成者。再者,PECVD可製造具有獨特組成及性質 之薄膜。所需性質如良好黏著性、低針孔密度、良好逐步 覆蓋、適當之電器性質及與精密線條圖案轉換製程,因此 使該薄膜可用於VLSI中。 PECVD需控制及使許多沉積參數最佳化,包含rf功率密度 、頻率及負載循環。沉積製程係依此等參數之複合及相互 依存性,以及一般之氣體組成、流動速率、溫度及壓力參 數而定。另外,針對LPCVD,PECVD法為表面反應限制,且 -24- 84564 200403764 因此需要適當之基材溫度控制,以確保均勾之薄膜厚度。 CVD系統通常含下列成分:氣體源、氣體飼入管線、氣 體進入系統之計量用質量流控制器、反應室或反應器、將 欲將薄膜沉積於其上之晶圓加熱用,及在部分類型之系統 中,藉由其他方法加入額外能量之方法,及溫度感應器。 LPCVD及PECVD系統亦含建立低壓且自室排放氣體之泵浦。 、 較好,本組合物係溶於溶劑中。本組合物之該溶液中所 , 用之適用溶劑包含在所需溫度下會揮發之任何適用之有機 、有機金屬、或無機分子之純的或混合物。適用之溶劑包 修 含非質子溶劑,例如環狀酮如環戊酮、環己酮、環庚酮及 環辛酮;環醯胺如N-烷基吡咯啶酮(其中之烷基具有約1至4 個碳原子);及N-環己基吡咯啶酮與其混合物。此處可使用 各種其他有機溶劑,只要其可協助溶解黏著促進劑,且同 時有效的控制作為塗料溶液之最終溶液之黏度即可。各種 協助之裝置如攪拌及/或加熱均可用於協助該溶解。其他適 用之溶劑包含甲基乙基酮、甲基異丁基酮、二丁基醚、環 狀二甲基聚矽氧烷、丁内酯、r - 丁内酯、2-庚酮、3-乙氧 基丙酸乙酯、1-甲基-2-吡咯啶酮、及丙二醇甲基醚乙酸酯 \ (PGMEA),及烴溶劑如杗、二甲苯、苯及甲苯。 本組合物可用於電器裝置中,尤其可用作與單一積體電 路(“1C”)晶片連結結合之層間介電質。積體電路晶片之表面 上一般具有許多層之本組合物及多層之金屬導體。其亦可 在不連續金屬導體或相同層或積體電路之平面中之導體間 包含本組合物之區。 84564 -25- 200403764 本薄膜可在基材上形成。此處之基材可包括任一種所需 實質固態之材料。最期望之基材層包括薄膜、玻璃、陶瓷 、塑膠、金屬或經塗佈之金屬、或複合材料。較佳具體例 中,基材包括砷化矽或坤化鎵模嘴或晶圓表面,封裝之表 面如銅、銀、鎳或金電鍍之導線框架中所見者,銅表面如 電路板或封裝連接線中所見者,穿孔壁或加強物之介面 (“銅”包含裸銅及其氧化物),聚合物為主之封裝或板介面 如聚亞酿胺為主之軟性封裝,導線或其他金屬合金焊接之 球型表面,氧化矽,氧基碳化矽,二氧化矽,碳化矽,氧 基氮化矽、氮化鈦、氮化鈕、氮化鎢、鋁、銅、钽、有機 矽氧烷、有機矽玻璃、及氟化之矽玻璃。依其他具體例, 基材包括慣用於封裝及電路板工業中之材料,如矽、銅、 玻璃及聚合物。由本組合物組成之電路板可在其表面上架 設各種導電之電路。電路板可包含各種補強物,如織布不 導電纖維或玻璃布。該電路板可為單面以及雙面。 本薄膜可用於積體電路製造之雙波紋(如銅)加工及基材 金屬(如链或銘/鎢)加工。本組合物可如Michael E· Thomas, “低keff介電質用之旋轉塗佈堆疊薄膜(Spin-On Stacked Films for Low keff Dielectrics)’’,Solid State Technology (July 2001)(在此提出供 參考)所教示用於所需之所有旋轉堆疊薄膜中。本組合物可 如共同受讓之美國專利第6,248,457B1 ; 5,986,045 ; 6,124,411及 6,303,733號之教示般,用於所有具有額外介電質之旋轉堆疊 薄膜中。 分析試驗方法 84564 -26- 200403764 介電常數:介電常數係藉由將薄鋁膜塗佈於硬化層上, 接著在1 MHz下進行電容-電壓測量,且以層之後度為準計 算k值。 折射係數:折射係數測量矽伴隨厚度測量,使用J.A.84564 -20- 200403764 The composition is prepared before coating on the substrate, so that it contains water in a proportion suitable for the initial precursor aging, but the proportion will not cause the precursor composition to be coated on the desired substrate Before aging or gelling. By way of example, when water is mixed in the precursor composition, the proportion of water in the composition including water depends on the molar ratio of water to Si atoms in the silicon-containing prepolymer from about 01 · to about 50: 1 exists. It is more preferably about 0.1 to about 10: 1, and most preferably about 0.5 to about 15: 1. Those skilled in the art should understand that the specific temperature range of cross-linking and removal of pore-forming agents from nano-porous dielectric films depends on the selected materials, substrates and the required nano-sized pore structure, and can be based on this. The regular operation of parameters and other parameters is used to measure the system. The coated substrate is treated, such as by heating, to crosslink the composition on the substrate to produce a gelled film. Cross-linking can be performed in step 由 by allowing the film to gel at a temperature of about 100t to about 25 (rc: heating for about 30 seconds to about 10 minutes. Skilled artisans should also understand that any additional techniques can be used as appropriate The hardening method known in the art includes hardening the film by exposing the film to sufficient energy such as electron beam energy, ultraviolet energy, microwave energy, etc., according to methods known in the art. If the synthetic solid or solid solid is used, the pore-forming agent can be removed. The latter should be sufficiently non-volatile so that it will not evaporate from the film before the thin film is cured. The pore-forming agent is used in step ⑷ by using a temperature of about At about 45 ° C, it is preferred to remove the gelled film by heating for about 3G seconds to about 1 hour at a temperature of about 150 ° to about 1 hour. An important feature of the present invention is that the gelation system of the better step ⑷ is at a temperature Do not lower than the heating temperature of step 。. Uses 84564 -21-200403764 This product can also include additional ingredients, such as adhesion promoter, anti-foaming sword, spring spring agent, flame retarder, pigment, plasticizer, stabilizer active agent .this The compound can be used for "1 η" private applications, such as thermal insulation, matrix materials for sealing ceramic materials, lightweight composite materials, insulation materials, anticorrosive coatings, ceramic powder powder binders and fire Delayed coating. ^ The composition is particularly useful as a dielectric substrate material in microchips, microchip modules, laminated circuit boards or printed wiring boards in microelectronic applications. This composition can also be used as an etch stopper Or hard mask. This film can be formed by solution technology, such as spray coating 'roll coating, dip coating, spin coating, flow casting and chemical vapor deposition. For chemical vapor deposition (CVD)', the composition is placed in CVD In the device, it is evaporated and introduced into the chamber containing the substrate to be coated. Evaporation can be achieved by heating the composition above its evaporation point, by vacuum or a combination of the above. Generally, evaporation is at atmospheric pressure. It is achieved at the given temperature, or at a lower temperature (close to room temperature) in vacuum. There are currently three types of CVD: atmospheric pressure krypton (ApcvD), low pressure krypton (LPCVD), and plasma enhanced CVD (pECVD). Each of these methods has advantages Point ° AP (: VI ^ is set at a temperature of about the reaction fork operation based on the mass transfer limit. The deposition is restricted by mass transfer. The temperature control of the deposition chamber is less stringent than other methods because of the relationship between the mass transfer process and temperature. Low. As for the rate at which the reactant reaches is directly related to its concentration in the overall gas, it is important to maintain a uniform phase of the reaction concentration in the overall gas adjacent to the wafer. Therefore, to ensure uniform film thickness on the wafer, Therefore, the reactors operating in the mass transfer restricted area need to be designed so that the surface of all the wafers 84564-22-200403764 are coated with the same flow of reactants. The most widely used APCVD reactor design is to horizontally arrange the wafers And is removed under a gas stream to provide a uniform supply of reactants. In contrast to the APCVD reactor, the LPCVD reactor operates in a reaction rate limited mode. According to the method of operating under reaction rate limiting conditions, the process temperature is an important parameter. In order to maintain uniform deposition in all reactors, the reactor temperature must be uniform in all reactors and on all wafer surfaces. The rate at which the deposited species reach the surface is not as important as constant temperature under conditions where the reaction rate is limited. Therefore, the LPCVD reactor does not need to be designed to supply unchanging reaction streams to all locations on the wafer surface. Under the low pressure of the LPCVD reactor, such as operating at moderate vacuum (30-250 Pa or 0.25 to 2.0 torr) and high temperature (550-600 ° C), the diffusivity of the deposited species will be approximately greater than that at atmospheric pressure. A factor of 1000 increases. The increased diffusivity is partially compensated by the fact that the distance at which the reactants must diffuse increases with the square root below the pressure. The actual effect is that the reactants are transported to the surface of the substrate and the increase in the size of the by-products leaving the surface of the substrate exceeds one level. The LPCVD reactor is one or two main structural designs: a horizontal tube reactor; and (b) a vertical tube isothermal reactor. Horizontal tubular, hot-wall reactors are the most widely used reactors in the VLSI process. It is used to deposit poly-Si, silicon nitride, and undoped and doped Si02 films. It has been found that such a wide range of applications is due to its excellent economy, yield, uniformity, and ability to use large diameter (eg 150 mm) wafers. The vertical flow isothermal LPCVD reactor can also be used for distributed gas feeding technology, so that each wafer can receive an equal amount of fresh reactants. The wafers can again be stacked side by side 84564 -23-200403764, but placed in a perforated quartz cage. The cage is placed under a long, holed quartz reaction gas injection tube, and there is one tube for each reaction gas. The gas is fixed by the ejection tube flowing through the hole of the cage vertically, passing through the wafer, parallel to the wafer surface and entering the exhaust slit under the cage. Use the size, number, and position of cage holes to control the flow of reactive gas to the wafer surface. By appropriately optimizing the design of the cage holes, the same amount of fresh reactant can be supplied to each crystal circle by the vertically adjacent ejection tubes. Therefore, this design can avoid the consumption of reactants on the wafer by the wafer fed with the tube reaction gas at the terminal, without the need for temperature drop, resulting in highly uniform deposition, and it is claimed that low particle contamination can be achieved. The third main CVD deposition method is PECVD. This method is classified not only by pressure zone, but also by its energy input method. In addition to starting and maintaining chemical reactions primarily with thermal energy, PECVD uses rf-induced flow emissions to pass energy into the reactant gas to keep the substrate temperature below the APCVD or LPCVD process temperature. Decreasing the substrate temperature is the main advantage of PECVD, which can prevent the film deposited on the substrate from having sufficient thermal stability to accept other methods of coating. PECVD also enables deposition rates to be improved over those achieved using thermal reactions. Furthermore, PECVD can produce films with unique composition and properties. Desired properties such as good adhesion, low pinhole density, good step-by-step coverage, proper electrical properties, and conversion process with precision line patterns make the film useful in VLSI. PECVD requires control and optimization of many deposition parameters, including rf power density, frequency, and load cycling. The deposition process depends on the compounding and interdependence of these parameters, and the general gas composition, flow rate, temperature and pressure parameters. In addition, for LPCVD, the PECVD method is a surface reaction limitation, and -24- 84564 200403764 therefore requires proper substrate temperature control to ensure uniform film thickness. A CVD system usually contains the following components: a gas source, a gas feed line, a mass flow controller for the metering of the gas into the system, a reaction chamber or reactor, a wafer heating on which a thin film is to be deposited, and some types In the system, the method of adding extra energy by other methods, and the temperature sensor. LPCVD and PECVD systems also include pumps that establish low pressure and emit gases from the chamber. The composition is preferably dissolved in a solvent. The suitable solvents used in this solution of the composition include any suitable organic, organometallic, or inorganic molecules that are pure or mixtures that will evaporate at the desired temperature. Suitable solvents include aprotic solvents, such as cyclic ketones such as cyclopentanone, cyclohexanone, cycloheptanone, and cyclooctanone; cyclopentamines such as N-alkylpyrrolidone (wherein the alkyl group has about 1 To 4 carbon atoms); and N-cyclohexylpyrrolidone and mixtures thereof. Various other organic solvents can be used here, as long as it can help dissolve the adhesion promoter, and at the same time effectively control the viscosity of the final solution as the coating solution. Various assisting devices such as stirring and / or heating can be used to assist the dissolution. Other suitable solvents include methyl ethyl ketone, methyl isobutyl ketone, dibutyl ether, cyclic dimethyl polysiloxane, butyrolactone, r-butyrolactone, 2-heptanone, 3- Ethyl ethoxypropionate, 1-methyl-2-pyrrolidone, and propylene glycol methyl ether acetate (PGMEA), and hydrocarbon solvents such as osmium, xylene, benzene, and toluene. The composition can be used in electrical devices, especially as an interlayer dielectric combined with a single integrated circuit ("1C") chip connection. The surface of an integrated circuit wafer generally has many layers of the composition and multiple layers of metal conductors. It may also include regions of the composition between discrete metal conductors or conductors in the same layer or plane of a integrated circuit. 84564 -25- 200403764 This film can be formed on a substrate. The substrate herein may include any desired substantially solid material. The most desirable substrate layers include films, glass, ceramics, plastics, metals or coated metals, or composite materials. In a preferred embodiment, the substrate includes a silicon arsenide or gallium die mouth or wafer surface, the package surface is as seen in a copper, silver, nickel, or gold-plated lead frame, and the copper surface is as a circuit board or package connection Seen in the wire, the interface of perforated walls or reinforcements ("copper" includes bare copper and its oxides), polymer-based packaging or board interfaces such as flexible packaging based on polyurethane, wires or other metal alloys Welded spherical surface, silicon oxide, oxysilicon carbide, silicon dioxide, silicon carbide, silicon oxynitride, titanium nitride, nitride button, tungsten nitride, aluminum, copper, tantalum, organosiloxane, Silicone glass and fluorinated silicon glass. According to other specific examples, the substrate includes materials commonly used in the packaging and circuit board industries, such as silicon, copper, glass, and polymers. A circuit board composed of the composition can be provided with various conductive circuits on its surface. The circuit board may contain various reinforcements such as woven non-conductive fibers or glass cloth. The circuit board can be single-sided as well as double-sided. This film can be used for double corrugation (such as copper) processing of integrated circuit manufacturing and substrate metal (such as chain or Ming / tungsten) processing. The composition can be, for example, Michael E. Thomas, "Spin-On Stacked Films for Low keff Dielectrics", Solid State Technology (July 2001) (herein referred for reference) ) Is used in all spin-stacked films required. This composition can be used in all of the teachings of commonly assigned U.S. Patent Nos. 6,248,457B1; 5,986,045; 6,124,411 and 6,303,733 for all dielectrics with additional dielectric properties. Rotary stacked films. Analysis test method 84564 -26- 200403764 Dielectric constant: The dielectric constant is obtained by coating a thin aluminum film on a hardened layer, and then performing capacitance-voltage measurement at 1 MHz, and using the layer after degree Calculate the value of k as it is. Refractive index: Refractive index measured with silicon thickness measurement, using JA

Woollam M-88光譜偏振光橢圓率測量儀進行。使用Cauchy模 型計算最適之Psi及(5。除非另有說明,折射係數係在633 nm v 之波長下測量(偏振光擴圓率測量儀之細節見於例如H.G. ^Woollam M-88 spectral polarized light ellipsometry was performed. The Cauchy model is used to calculate the optimal Psi and (5. Unless otherwise stated, the refractive index is measured at a wavelength of 633 nm v (details of polarized light roundness measuring instruments can be found in, for example, H.G. ^

Thompkins 及 William A. McGahan,John Wiley and Sons,Inc.,1999)之 “光譜偏振光橢圓率測量儀及反射計”)。 鲁 平均孔隙直徑:在Micromeretics ASAP 2000自動等溫N2吸收 裝置上,使用UHP(超高純度工業用氣體)N2,以浸潰在77°Κ 之液氮槽中之樣品管中之樣品,測量多孔性樣品之Ν2等溫 線。 為製備樣品,先使用標準加工條件,使材料沉積在硬晶 圓上。針對各樣品,係以約6000埃之薄膜厚度製備三晶圓 。接著以刮鬍刀片刮除自晶圓移除薄膜。使此等粉末狀樣 品於稱重前在烘箱中180°C預烘乾,小心地將粉末倒入10毫 籲-米内徑之樣品管中,接著在180°C及0·01 Torr下除氣&gt;3小時。 ' 接著使用5秒平衡間隔再自動測量吸附及去吸附之n2吸附 ,除非分析顯示需要長時間。測量等溫所需時間係與樣品 之質量、樣品之孔隙體積、測量之數據點數目、平衡間隔 及P/Po忍受度(P為樣品管中樣品之實際壓力,p〇為設備外 之周圍壓力)成正比。設備測量N2等溫線且化出n2對P/Po。 顯現之 BET (S.呈runauer,P· H· Emmett,g·工eller; j· Am· Chem· Soc. 84564 -27- 200403764 60, 309-319 (1938)中揭示之固體表面之多層氣體吸附用之 Brunauer,Emmett,Teller法)表面積係使用BET理論,使用提供 R2fit〉0.9999之BET方程式之線性段,自N2吸收等溫線之較低 P/Po區計算。 孔隙體積係在相對壓力P/Po值下(通常P/Po〜0.95,其為冷 凝完全之等溫平面區),假設吸收凡之密度與液態N2相同, 且所有孔隙均充填在該P/Po下之冷凝N2,由所吸收之N2體積 計算。 孔隙尺寸分布係使用Kelvin方程式理論,使用自N2等溫線 之 BJH (E. P. Barret,L· G· !oyner,P· P. Halenda; J· Am· Chem. Soc.,73, 373-380 (1951))孔隙尺寸分布,由N2等溫線之吸附壁計算。此 使用Kelvin方程式,其曲線與蒸氣壓之壓制有關,及Halsey 方程式,其敘述吸收之N2單層之厚度對P/Po,以將冷凝之N2 體積對P/Po轉化成特殊範圍之孔隙尺寸之孔隙體積。 平均圓柱體孔隙直徑D為具有如樣品之相同外顯BET表面 積Sa (m2/g)及孔隙體積Vp (cc/g)之圓柱體直徑,因此D (nm)= 4000 Vp/Sa。 以下非限制用實例係用於說明本發明。 實例1 該實例顯示以具有高濃度鈉之成孔劑製造奈米多孔性矽 石。前驅物係藉由在100毫升圓底瓶(含磁石攪拌棒)中合併 10克四乙醯氧基矽烷、10克甲基三乙醯氧基矽烷及17克丙 二醇甲基乙基乙酸酯(PGMEA)製備。將此等成分合併於Nr 環境(N2套袋)中。該瓶亦與N2環境相連以避免環境濕氣進入 -28- 84564 200403764 溶液中(標準溫度及壓力)。 反應混合物加熱至80。(:,接著將L5克水加於瓶中。水添 加完成後,使反應混合物冷卻至周圍溫度,接著添加426克 之聚乙二醇單甲基醚(“PE0”; MW550 amu)(具有&gt;3〇〇卩沖之Na) 作為成孔劑,且再持續攪拌2小時。隨後,使所得溶液經 〇·2微米過濾器過濾,獲得下一步驟用之前驅物溶液主批次 。再將孩溶液沉積於一系列8_吋矽晶圓上,各晶圓均在旋 轉台上,且在2500 rpm下旋轉30秒。前驅物中存在之水導致 薄膜塗層隨著晶圓插入第一烘箱中之時間而實質的冷凝。 如下所述之插入第一烘箱中係發生在旋轉完成之1〇秒中内 。各經塗佈之晶圓再移轉入連續預設定特定溫度之一系列 洪箱中各一分鐘。該實例中,有三個洪箱,且預設定之洪 箱溫度分別為8(TC、175t及30{rc。當各晶圓經過三個別烘 箱之各個時’㈣藉由此等連續加熱驅除。各晶圓在接受 二烘箱逐步加熱處理後冷卻,且使用偏振光_率測量製 造之介電質薄膜,以測定其厚度及折射係數。各經薄膜塗 佈疋晶圓再於氮氣流及贼下進—步硬化—小時。由本發 明之液態前驅物製備之非多孔性薄膜之折射係數為Μ,: k除氣為3.2。比較上,空氣之折射係數為1〇。本發明之太米 多孔性薄膜之孔隙度因此與其空氣之體積成正比。薄^之 烘烤厚度為5920埃,烘烤折射係數為1 234,硬化 埃,且硬化折射係數為丨.231。產生之硬化薄 又'、 、a 王 &lt; 硬化薄腱之孔隙詹约 為43%(見下表之第”頁)。表中, 。、 r潯膜係在周圍條件 U/皿u)下測量。以周圍電容值為主之介電常數稱之 84564 -29- 200403764 為k周圍。晶圓在200°C加熱板上加熱2分鐘,以去除吸收之 水氣後,再度測量薄膜之電容。以除水氣為主之介電常數 稱之為k除氣。 實例2(比較用) 該實例顯示以具有低濃度鈉之成孔劑製造奈米多孔性矽 石。 具有高濃度鈉之粗PEO(聚乙二醇單甲基醚,MW=550)係 藉由使粗PEO與水依50:50重量比混合純化。使該混合物通 過離子交換樹脂移除金屬。收集滤液且進行真空蒸館,移 除水以製造純的、低金屬PEO(具有&lt;100 ppb之Na)。接著重 複實例1之程序,但以低金屬PEO取代高金屬PEO。經估算 形成之k除氣值為3.03,薄膜基本上崩塌且孔係度僅約7%, 相較於實例1 (比較例)下降43%。薄膜之烘烤厚度為4179埃, 烘烤折射係數為1.353,硬化厚度為3875埃,且硬化折射係數 為1.331(見下表第2項)。 實例3 重複實例2,但該實例添加鈉陽離子(氫氧化鈉(見第3項) 或硫酸鈉(見第4項)),以恢復低的k值。將氫氧化鈉(NaOH, 23 ppm)或硫酸#3 (Na2S〇4, 40 ppm)添力ir於離子交換之PEO及前驅 物主批次中。藉由在2400 rpm或3500 rpm下旋轉塗佈將薄膜沉 積於晶圓上。旋轉塗佈後,薄膜在溫度80°C、175°C及300°C 之三加熱板中加熱。烘烤後,使薄膜在氮氣流及425°C下硬 化一小時。k之結果及後硬化薄膜之R.I.列於下表中。 實例4 -30- 84564 200403764 重複實例2,但該實例添加四有機銨(TMAA)(第5, 6及7項) 、TMAH(第8項)或TBAA(第9項)離子,以恢復低k。將各種 量之TMAA添加於經離子交換之PEO及前驅物主批次中。部 分情況下,將小量之甲基三乙醯氧基矽烷(MTAS,1%,見 第6項)添加於溶液中,作為就地表面改質劑,使表面低親 水性。藉由在2400 rpm或3500 rpm下將薄膜沉積在晶圓上。旋 轉塗佈後,使薄膜在溫度80°C、175°C及300°C之加熱板上各 加熱一分鐘。烘烤後使薄膜在氮氣流及425°C下硬化一小時 。針對5及6項,平均孔係尺寸直徑為2.5 nm。後硬化薄膜之 k及R.I·結果列於下表中。顯示當銨離子之濃度大於約65XHT9 莫耳/克溶液時,k值低於2.5,相當於約3 ppm(重量)之TMAA。 實例5 該實例顯示由具有低濃度鈉之成孔劑及市售甲基矽氧烷 聚合物(Honeywell ACCUGLASS⑧ SPIN-ON GLASS 512B)製備之奈 米多孔性矽石之製造。 具有高濃度鈉之粗PEO(聚乙二醇單甲基醚,MW=550)係 藉由使粗PEO與水依50:50重量比混合純化。使該混合物通 過離子交換樹脂移除金屬。收集濾液且進行真空蒸餾,移 除水以製造純的、低金屬PEO(具有&lt;100 ppb之Na)。將所得 PEO (4.88 克)及丁醇(48 克)與 ACCUGLASS® SPIN-ON GLASS 512B (43克)混合。因此,使所得溶液經過0.2微米過濾器過濾, 獲得下一步驟用前驅物溶液主批次。再將該溶液沉積於一 系列8-叶石夕晶圓上,各晶圓均在旋轉台上,且在3000 rpm下 旋轉30秒。前驅物中存在之水導致薄膜塗層隨著晶圓插入 -31 - 84564 200403764 第一烘箱中之時間而實質的冷凝。如下所述之插入第一烘 箱中係發生在旋轉完成之10秒中内。各經塗佈之晶圓再移 轉入連續預設定特定溫度之一系列烘箱中各一分鐘。該實 例中,有三個烘箱,且預設定之烘箱溫度分別為80°c、175°c 及300°C。當各晶圓經過三個別烘箱之各個時,PEO藉由此 等連續加熱驅除,各晶圓在接受三烘箱逐步加熱處理後冷 卻,且使用偏振光橢圓率測量製造之介電質薄膜,以測定 其厚度及折射係數。各經薄膜塗佈之晶圓再於氮氣流及425 °C下進一步硬化一小時。薄膜崩塌且無法形成多孔性結構 。薄膜之烘烤厚度為1690埃,烘烤折射係數為1.395,硬化厚 度為1615埃,且硬化折射係數為1.367。產生之硬化薄膜之孔 隙度約為5°/。(見下表之第10項)。 實例6 重複實例5,但該實例添加四有機銨(TMAA(第11項))離子 ,以恢復低k。將TMAA (10 ppm)添加於離子交換之PEO (3.64 克)、丁醇(13 克)及 ACCUGLASS® SPIN-ON GLASS 512B (25克) 中。以2000 rpm之旋轉塗佈,將薄膜沉積在晶圓上。旋轉塗 佈後,薄膜分別在溫度125°C、200°C及350°C之三加熱板上加 熱一分鐘。烘烤後,使薄膜在氮氣流及425°C下硬化一小時 。後硬化薄膜之k及R.I.結果列於下表中。產生之應化薄膜 之孔隙度約40%。平均孔隙尺寸直徑為2.5 nm。 表1 項次 添加劑 濃度Ppm PEO K周圍 k除氣 △ k 最終之 NaPpb 硬化 之 R.I. 硬化之厚 度,埃 1 0 粗品 2.60 2.36 0.24 285 1.231 5619 2 0 低金屬 3.62 3.03 0.59 &lt;25 1.331 3875 84564 -32- 200403764 3 40 (Na2S04) 低金屬 2.21 2.10 0.11 1.232 7244 4 23 (NaOH) 低金屬 2.24 2.21 0.03 1.246 5479 5 6 (TMAA) 低金屬 2.34 2.23 0.11 43 1.209 6127 6 6 (TMAA) 低金屬 2.24 2.13 0.11 43 1.218 6319 7 3 (TMAA) 低金屬 2.65 2.38 0.27 95 1.248 6495 8 22 (TMAH) 低金屬 2.27 2.10 0.17 &lt;25 1.215 7871 9 100 (TBAA) 低金屬 2.55 2.27 0.28 65 1.213 7716 10 0 低金屬 n/a N/a n/a &lt;25 1.367 1615 11 10 (TMAA) 低金屬 2.41 2.24 0.17 &lt;25 1.215 6467 實例7 以下實例(表II第1項)顯示縮合(亦以之為矽烷醇基之交 聯)反應在300°C及沒有TMAA下受損。為說明起見,並未添 加成孔劑。前驅物係藉由在100毫升圓底瓶(含磁石攪拌棒) 中合併10克四乙醯氧基矽烷、10克甲基三乙醯氧基矽烷及 17克丙二醇甲基乙基乙酸酯(PGMEA)製備。將此等成分合併 於Nr環境(N2套袋)中。該瓶亦與N2環境相連以避免環境濕 氣進入溶液中(標準溫度及壓力)。反應混合物加熱至80°C, 接著將1.5克水加於瓶中。水添加完成後,使反應混合物冷 卻至周圍溫度,接著使所得溶液經0.2微米過濾器過漉,獲 得下一步驟用之前驅物溶液主批次。再將該溶液沉積於一 系列8-对石夕晶圓上,各晶圓均在旋轉台上,且在2500卬m下 旋轉30秒。前驅物中存在之水導致薄膜塗層隨著晶圓插入 第一加熱板上之時間而實質的冷凝。如下所述之插入第一 84564 -33 - 200403764 加熱板上係發生在旋轉完成之10秒中内。各經塗佈之晶圓 再移轉入連續預設定特定溫度之一系列加熱板上各一分鐘 。該實例中,有三個烘箱,且預設定之烘箱溫度分別為80°c 、175°C及300°C。各晶圓在接受三烘箱逐步加熱處理後冷卻 ,且使用偏振光橢圓率測量製造之介電質薄膜,以測定其 厚度及折射係數,且使用FTIR測量矽烷醇(SiOH,v:3100-3800 〇11-1)對甲基(0«3,\/:2978 〇11-1)面積比。針對111為1.41±0.01之3 kA薄膜,發現之(Si)OH對CH3大於20。經烘烤薄膜之FTIR光 譜說明大量之矽烷醇(見圖1)。各經薄膜塗度之晶圓在於425 °C氮氣流下進一步硬化一小時。所得薄膜之(Si)OH對CH3比 為2。 實例8 重複實例7,但該實例添加四有機銨(TMAA)(第2項)。該 實例說明在300°C下之縮合反應係藉由存在之TMAA催化。藉 由在2400 rpm下旋轉塗佈經薄膜沉積在晶圓上。旋轉沉積後 ,使薄膜在溫度為80°C、175°C及300°C之加熱板上分別加熱 一分鐘。烘烤後,以FT1R分析薄膜,以測定矽烷醇(SiOH)對 甲基(CH3)面積比。針對RI為1.41之3 kA薄膜,發現之矽烷醇 ((SiOH)對甲基(CH3)比約為4。使矽烷醇含量下降較佳係藉由 薄膜之FTIR光譜說明。(見圖1)。圖1顯示矽烷醇含量下降 之FTIR光譜:後烘烤項次1&gt;&gt;&gt;後烘烤項次2〉後硬化,項次 1 =後硬化項次2。 各經薄膜塗佈之晶圓再於425°C之氮氣流下進一步硬化一 小時。所得薄膜之(Si)OH對CH3之比為2。 84564 . -34- 200403764Thompkins and William A. McGahan, John Wiley and Sons, Inc., 1999) "Spectral Polarized Light Ellipsometer and Reflectometer"). Lu average pore diameter: On a Micromeretics ASAP 2000 automatic isothermal N2 absorption device, UHP (Ultra High Purity Industrial Gas) N2 was used to immerse a sample in a sample tube in a liquid nitrogen tank at 77 ° K to measure the porosity Sexual N2 isotherms. To prepare the samples, the materials were first deposited on hard crystal circles using standard processing conditions. For each sample, three wafers were prepared with a film thickness of about 6000 Angstroms. The film was then removed from the wafer with a razor blade. Pre-dry these powder samples in an oven at 180 ° C before weighing. Carefully pour the powder into a 10 millimeter-meter inner diameter sample tube, then degas at 180 ° C and 0.01 Torr &gt; 3 hours. 'Then use the 5-second equilibration interval to automatically measure the adsorption and desorption of n2 adsorption, unless analysis shows that it takes a long time. The time required for isothermal measurement is the mass of the sample, the pore volume of the sample, the number of measured data points, the equilibrium interval, and the P / Po tolerance (P is the actual pressure of the sample in the sample tube, and p0 is the ambient pressure outside the device ) Is proportional. The device measures the N2 isotherm and converts n2 to P / Po. Appearance of BET (S. Cheng runauer, P.H. Emmett, G. Geller; J. Am. Chem. Soc. 84564 -27- 200403764 60, 309-319 (1938) revealed multilayer gas adsorption on solid surfaces The Brunauer, Emmett, and Teller methods are used.) The surface area is calculated from the lower P / Po region of the N2 absorption isotherm using the linear segment of the BET equation that provides R2fit> 0.9999. The pore volume is under the relative pressure P / Po value (usually P / Po ~ 0.95, which is the isothermal plane area with complete condensation). It is assumed that the density of the absorption element is the same as that of liquid N2, and all pores are filled in the P / Po The condensing N2 below is calculated from the volume of N2 absorbed. The pore size distribution is based on the Kelvin equation theory, using BJH from the N2 isotherm (EP Barret, L. G.! Oyner, P. P. Halenda; J. Am. Chem. Soc., 73, 373-380 (1951 )) The pore size distribution is calculated from the adsorption wall of the N2 isotherm. This uses the Kelvin equation, the curve of which is related to the suppression of vapor pressure, and the Halsey equation, which describes the thickness of the absorbed N2 monolayer versus P / Po to convert the condensed N2 volume versus P / Po into a special range of pore sizes. Pore volume. The average cylinder pore diameter D is the diameter of a cylinder having the same apparent BET surface area Sa (m2 / g) and pore volume Vp (cc / g) as the sample, so D (nm) = 4000 Vp / Sa. The following non-limiting examples are provided to illustrate the invention. Example 1 This example shows the production of nanoporous silica with a pore former having a high concentration of sodium. The precursor was obtained by combining 10 g of tetraethoxysilane, 10 g of methyl triethoxysilane and 17 g of propylene glycol methyl ethyl acetate (in a 100 ml round-bottomed bottle (including a magnetic stir bar)). (PGMEA). Combine these ingredients in an Nr environment (N2 bagging). The bottle is also connected to the N2 environment to prevent ambient moisture from entering -28- 84564 200403764 solution (standard temperature and pressure). The reaction mixture was heated to 80 ° C. (:, Then add 5 grams of water to the bottle. After the addition of water is complete, cool the reaction mixture to ambient temperature, then add 426 grams of polyethylene glycol monomethyl ether ("PE0"; MW550 amu) (with &gt; (3,000,000 Na) was used as a pore-forming agent, and continued to stir for another 2 hours. Subsequently, the resulting solution was filtered through a 0.2 micron filter to obtain the main batch of the precursor solution for the next step. The solution was deposited on a series of 8-inch silicon wafers, each wafer was on a rotating table and rotated at 2500 rpm for 30 seconds. The water present in the precursor caused the thin film coating to be inserted into the first oven with the wafer Substantially condensing in time. Insertion into the first oven as described below occurs within 10 seconds of completion of the spin. Each coated wafer is then transferred to a series of flood boxes that are continuously preset a specific temperature. One minute each. In this example, there are three flood boxes, and the preset flood box temperatures are 8 (TC, 175t, and 30 {rc.) When each wafer passes through each of three separate ovens. Expulsion by heating. Each wafer is cooled after being gradually heated by two ovens, and The manufactured dielectric film is measured by polarized light rate to determine its thickness and refractive index. Each film is coated with a wafer and then under nitrogen flow and thief-step hardening-hour. Prepared from the liquid precursor of the present invention The non-porous film has a refractive index of M, and k has a degassing ratio of 3.2. In comparison, the refractive index of air is 10. The porosity of the porous rice film of the present invention is therefore directly proportional to the volume of its air. Thin ^ The baking thickness is 5920 angstroms, the baking refractive index is 1 234, the hardened angstroms, and the hardened refractive index is 丨 .231. The resulting hardened thin and thin, the pores of the hardened thin tendon are about 43%. (See the "page" of the table below.) In the table,., R is measured under the surrounding conditions (U / U u). The dielectric constant based on the surrounding capacitance is called 84564 -29- 200403764. The wafer is heated on a 200 ° C heating plate for 2 minutes to remove the absorbed water vapor, and then the capacitance of the film is measured again. The dielectric constant mainly dewatering is called k degassing. Example 2 (comparative ) This example shows the production of nanoporous silica with a pore former with a low concentration of sodium. Stone. Crude PEO (polyethylene glycol monomethyl ether, MW = 550) with a high concentration of sodium is purified by mixing crude PEO with water in a weight ratio of 50:50. The mixture is removed by ion exchange resin The filtrate was collected and vacuum-evaporated, and water was removed to make a pure, low-metal PEO (with <100 ppb of Na). The procedure of Example 1 was then repeated, but the high-metal PEO was replaced with a low-metal PEO. It was estimated to form The outgassing value of k is 3.03, the film basically collapses and the porosity is only about 7%, which is 43% lower than that of Example 1 (comparative example). The baking thickness of the film is 4179 angstroms and the baking refractive index is 1.353. The hardened thickness is 3875 angstroms and the hardened refractive index is 1.331 (see item 2 in the table below). Example 3 Example 2 was repeated except that sodium cations (sodium hydroxide (see item 3) or sodium sulfate (see item 4)) were added to restore a low k value. Add sodium hydroxide (NaOH, 23 ppm) or sulfuric acid # 3 (Na2SO4, 40 ppm) to the ion-exchanged PEO and precursor master batch. The film was deposited on the wafer by spin coating at 2400 rpm or 3500 rpm. After spin coating, the film was heated on three hot plates at temperatures of 80 ° C, 175 ° C and 300 ° C. After baking, the film was hardened for one hour under a stream of nitrogen at 425 ° C. The results of k and the R.I. of the post-hardened film are listed in the table below. Example 4 -30- 84564 200403764 Example 2 was repeated, but this example added tetraorganic ammonium (TMAA) (items 5, 6 and 7), TMAH (item 8) or TBAA (item 9) ions to restore low k . Various amounts of TMAA were added to the ion-exchanged PEO and precursor batches. In some cases, a small amount of methyltriethoxysilane (MTAS, 1%, see item 6) was added to the solution as an in-situ surface modifier to make the surface low in hydrophilicity. By depositing the thin film on the wafer at 2400 rpm or 3500 rpm. After spin coating, the films were heated on heating plates at temperatures of 80 ° C, 175 ° C, and 300 ° C for one minute each. After baking, the film was hardened for one hour under a stream of nitrogen at 425 ° C. For items 5 and 6, the average pore size diameter is 2.5 nm. The k and R.I. results of the post-cured film are shown in the table below. It has been shown that when the concentration of ammonium ion is greater than about 65XHT9 mole / g solution, the k value is less than 2.5, which is equivalent to about 3 ppm (weight) TMAA. Example 5 This example shows the manufacture of nanoporous silica prepared from a porogen with a low concentration of sodium and a commercially available methylsiloxane polymer (Honeywell ACCUGLASS (R) SPIN-ON GLASS 512B). Crude PEO (polyethylene glycol monomethyl ether, MW = 550) with a high concentration of sodium is purified by mixing crude PEO with water in a weight ratio of 50:50. The mixture was passed through an ion exchange resin to remove the metal. The filtrate was collected and subjected to vacuum distillation, and water was removed to make pure, low-metal PEO (with &lt; 100 ppb of Na). The resulting PEO (4.88 g) and butanol (48 g) were mixed with ACCUGLASS® SPIN-ON GLASS 512B (43 g). Therefore, the resulting solution was filtered through a 0.2 micron filter to obtain a main batch of precursor solution for the next step. This solution was then deposited on a series of 8-leaf stone wafers, each wafer was on a rotating table and rotated at 3000 rpm for 30 seconds. The presence of water in the precursor causes the film coating to substantially condense as the wafer is inserted in the first oven at -31-84564 200403764. Insertion into the first oven as described below occurred within 10 seconds of completion of the rotation. Each coated wafer is then transferred to a series of ovens that are continuously preset to a specific temperature for one minute each. In this example, there are three ovens, and the preset oven temperatures are 80 ° c, 175 ° c, and 300 ° C. When each wafer passes through each of three separate ovens, PEO is expelled by such continuous heating. Each wafer is cooled after being gradually heated in the three ovens, and the dielectric thin film manufactured by polarized ellipticity measurement is used to determine Its thickness and refractive index. Each film-coated wafer was further hardened for one hour under a stream of nitrogen at 425 ° C. The film collapsed and could not form a porous structure. The baked thickness of the film was 1690 angstroms, the baked refractive index was 1.395, the hardened thickness was 1615 angstroms, and the hardened refractive index was 1.367. The porosity of the resulting hardened film was about 5 ° /. (See item 10 in the table below). Example 6 Example 5 was repeated, but this example added tetraorganic ammonium (TMAA (item 11)) ions to restore low k. TMAA (10 ppm) was added to ion-exchanged PEO (3.64 g), butanol (13 g), and ACCUGLASS® SPIN-ON GLASS 512B (25 g). The film was deposited on the wafer by spin coating at 2000 rpm. After spin coating, the film was heated on three hot plates at 125 ° C, 200 ° C, and 350 ° C for one minute. After baking, the film was allowed to harden for one hour under a stream of nitrogen at 425 ° C. The k and R.I. results of the post-cured film are shown in the table below. The porosity of the resulting applied film is about 40%. The average pore size diameter is 2.5 nm. Table 1 Sub-additive concentration Ppm PEO K around k degassing △ k final NaPpb hardened RI hardened thickness, Angstrom 1 0 crude 2.60 2.36 0.24 285 1.231 5619 2 0 low metal 3.62 3.03 0.59 &lt; 25 1.331 3875 84564 -32 -200403764 3 40 (Na2S04) Low metal 2.21 2.10 0.11 1.232 7244 4 23 (NaOH) Low metal 2.24 2.21 0.03 1.246 5479 5 6 (TMAA) Low metal 2.34 2.23 0.11 43 1.209 6127 6 6 (TMAA) Low metal 2.24 2.13 0.11 43 1.218 6319 7 3 (TMAA) Low metal 2.65 2.38 0.27 95 1.248 6495 8 22 (TMAH) Low metal 2.27 2.10 0.17 &lt; 25 1.215 7871 9 100 (TBAA) Low metal 2.55 2.27 0.28 65 1.213 7716 10 0 Low metal n / a N / an / a &lt; 25 1.367 1615 11 10 (TMAA) Low metal 2.41 2.24 0.17 &lt; 25 1.215 6467 Example 7 The following example (item 1 of Table II) shows condensation (also referred to as silanol-based cross-linking) The reaction was impaired at 300 ° C without TMAA. For illustration purposes, no porogen was added. The precursor was obtained by combining 10 g of tetraethoxysilane, 10 g of methyl triethoxysilane and 17 g of propylene glycol methyl ethyl acetate (in a 100 ml round-bottomed bottle with a magnetic stir bar) (PGMEA). Combine these ingredients in the Nr environment (N2 bagging). The bottle is also connected to the N2 environment to prevent ambient moisture from entering the solution (standard temperature and pressure). The reaction mixture was heated to 80 ° C, and then 1.5 g of water was added to the bottle. After the addition of water was completed, the reaction mixture was cooled to ambient temperature, and the resulting solution was passed through a 0.2 micron filter to obtain a main batch of precursor solution for the next step. This solution was then deposited on a series of 8-pair Shi Xi wafers, each wafer was on a rotating table and rotated at 2500 卬 m for 30 seconds. The presence of water in the precursor causes the film coating to substantially condense as the wafer is inserted into the first hot plate. Insertion of the first 84564 -33-200403764 heating plate as described below occurred within 10 seconds of completion of the rotation. Each coated wafer is then transferred to a series of hot plates continuously preset to a specific temperature for one minute each. In this example, there are three ovens, and the preset oven temperatures are 80 ° C, 175 ° C, and 300 ° C, respectively. Each wafer was cooled after being gradually heated in a three-oven oven, and a dielectric thin film manufactured by measuring the ellipticity of polarized light was used to determine its thickness and refractive index, and silanol (SiOH, v: 3100-3800) was measured using FTIR. 11-1) Area ratio of p-methyl (0 «3, \ /: 2978 〇11-1). For the 3 kA thin film with 111 of 1.41 ± 0.01, it was found that (Si) OH has a CH3 greater than 20. The FTIR spectrum of the baked film indicates a large amount of silanol (see Figure 1). Each film-coated wafer was further hardened for one hour under a nitrogen stream at 425 ° C. The (Si) OH to CH3 ratio of the obtained film was 2. Example 8 Example 7 was repeated, but this example added tetraorganic ammonium (TMAA) (item 2). This example illustrates that the condensation reaction at 300 ° C is catalyzed by the TMAA present. The film was deposited on the wafer by spin coating at 2400 rpm. After spin deposition, the films were heated on hot plates at 80 ° C, 175 ° C, and 300 ° C for one minute. After baking, the film was analyzed by FT1R to determine the area ratio of silanol (SiOH) to methyl (CH3). For a 3 kA film with an RI of 1.41, the silanol ((SiOH) to methyl (CH3) ratio was found to be about 4. The reduction in silanol was better explained by the FTIR spectrum of the film (see Figure 1). Figure 1 shows the FTIR spectrum of the decrease in silanol content: Post-baking term 1 &gt; &gt; Post-baking term 2> Post-curing, term 1 = Post-curing term 2. Each film-coated wafer It was further hardened for one hour under a nitrogen stream at 425 ° C. The (Si) OH to CH3 ratio of the obtained film was 2. 84564. -34- 200403764

RI SiO-H/SiC-H, 1.41 2 1.41 2 1 &quot;、 . — Ύ勹干乂 I土六月旦双返,但 熟習本技藝者應可輕易了解各種改變及改質均不離本發明 &lt;精神及範圍。且希望申請專利範圍將涵蓋先前敘述之揭 示具體例,其改變,及所有對等例。 【圖式簡單說明】 圖1顯示實例8薄膜之FTIR光譜,其中之矽烷醇含量下 降··後烘烤通道1&gt;&gt;&gt;後烘烤通道2&gt;後硬化,通道卜後硬化 通道2。 84564 35-RI SiO-H / SiC-H, 1.41 2 1.41 2 1 &quot;,. — Ύ 勹 乾 乂 I 土 一 回 一月, but those skilled in the art should be able to easily understand the various changes and modifications without departing from the invention &lt; Spirit and scope. It is hoped that the scope of patent application will cover the specific examples of disclosure, their changes, and all equivalent examples. [Brief description of the figure] Fig. 1 shows the FTIR spectrum of the thin film of Example 8, in which the content of silanol is decreased ... Post-baking channel 1 &gt; &gt; Post-baking channel 2 &gt; Post-hardening, channel 2 and post-hardening channel 2. 84564 35-

Claims (1)

200403764 拾、申請專利範圍: 1. -種製造奈米多孔性矽石介電質薄膜之方法,包括 ⑻製備包括含矽預聚物、成孔劑、 /匕 ^ ^ „ 及選自包含鏘化合物 及親核物之無金屬離子觸媒之組合物; (b)以組合物塗佈基材,形成薄膜; (c)使組合物交聯,產生膠凝薄膜,及 ⑹在一定溫度下加熱該膠凝薄膜一段期間 移除所有該成孔劑。 貫質的有效 2. 3. 4. 5. 6.200403764 Scope of patent application: 1. A method for manufacturing nano-porous silica dielectric thin film, including: preparing a silicon-containing prepolymer, a pore-forming agent, / ^ ^ ^ and selected from the group consisting of a rhenium compound And nucleophile-free metal ion catalyst composition; (b) coating the substrate with the composition to form a thin film; (c) cross-linking the composition to produce a gel film, and then heating the composition at a certain temperature Remove all of the pore formers for a period of time from the gelled film. Consistently effective 2. 3. 4. 5. 6. 如申睛專利範圍第1項之方法,並中太 ^ T 丁、米多孔性碎石介電 質薄膜之孔隙體積以薄膜之體積為準為約5 %至約㈣。 如申請專利範園第!項之方法,其中所得奈米多孔性碎石 介電質薄膜之介電常數約為3或以下。 如申請專利範圍第!項之方法,其中該奈米多爾石介 電質薄膜之平均孔隙直徑在約lnm至約3〇nm之範圍内。 如申請專利範圍第1項之方法,其中該觸媒係選自由按化 合物、胺、鱗化合物及膦化合物組成之群組。 如申請專利範圍第1項之方法,其中該觸媒係選自由四有 機銨化合物及四有機鱗化合物組成之群組。 如申請專利範圍第1項之方法,其中該觸媒係選自由四甲 基铵乙鹽、四甲基铵氫氧化物、四丁基铵乙酸鹽、三 笨基胺、三辛基胺、三-十二烷基胺、三乙醇胺、四甲基 鱗乙酸鹽、四甲基鱗氫氧化物、三苯基膦、三甲基膦、 三辛基膦及其結合物組成之群組。 如申請專利範圍第1項之方法,其中該組合物尚包括可加For example, the method of claim 1 in the patent scope, and the pore volume of the porous dielectric stone film of China and Japan, based on the volume of the film, is about 5% to about ㈣. Such as applying for a patent Fan Yuandi! The method according to item 2, wherein the dielectric constant of the obtained nanoporous crushed-stone dielectric film is about 3 or less. For example, the method of claim 1 in the patent scope, wherein the average pore diameter of the nanomite stone dielectric film is in a range of about 1 nm to about 30 nm. For example, the method of claim 1 in the patent scope, wherein the catalyst is selected from the group consisting of a compound, an amine, a scale compound, and a phosphine compound. For example, the method of claim 1 in the patent scope, wherein the catalyst is selected from the group consisting of four organic ammonium compounds and four organic scale compounds. For example, the method of claim 1, wherein the catalyst is selected from the group consisting of tetramethylammonium ethyl salt, tetramethylammonium hydroxide, tetrabutylammonium acetate, tritylamine, trioctylamine, -A group consisting of dodecylamine, triethanolamine, tetramethylphosphonium acetate, tetramethylphosphonium hydroxide, triphenylphosphine, trimethylphosphine, trioctylphosphine and combinations thereof. For example, if the method of claim 1 is applied for, the composition further includes 84564 200403764 速組合物交聯之非金屬性及親核性之添加劑。 9·如申請專利範圍第1項之方法,其中該組合物尚包括可加 速組合物交聯之親核性添加劑,該添加劑係選自由二甲 基礙、二甲基甲臨胺、六甲基磷三酿胺、胺及其結合物 組成之群組。 10·如申請專利範圍第1項之方法,其中該組合物尚包括水, 且水與Si之莫耳比為約0.1:1至約5〇:1。 U·如申請專利範圍第1項之方法,其中該組合物包括下式I 之含矽預聚物: Rx - Si - Ly (式 I) 其中X為0至約2之整數,且y為4·χ(約2至約4之整數); R係獨立選自由烷基、芳基、氫、伸烷基、伸芳基及其結 合物組成之群組; L為負電性基團,其係獨立選自由烷氧基、羧基、乙醯氧 基、胺基、醯胺基、_化物、異氰酸酯基及其結合物組 成之群組。 12·如申请專利範圍第n項之方法,其中該組合物包括藉由 使式I之預聚物縮合形成之聚合物,其中該聚合物之數量 平均分子量為約150至約300,〇〇〇 amu。 13·如申請專利範圍第丨項之方法,其中該組合物包括選自由 乙酿氧基石夕垸、乙氧基矽烷、甲氧基矽烷及其結合物組 成之群組之含矽預聚物。 14·如申請專利範圍第i項之方法,其中該組合物包括選自由 四乙醯氧基矽烷、Ci至約c6烷基或芳基-三乙醯氧基矽烷 84564 200403764 及其結合物組成之群組之含砂預聚物。 15. 如申請專利範圍第14項之 万法,其中該三乙醯氧基矽烷 為甲基三乙驢氧基碎燒。 16. 如申請專利範圍第之方法,其中該組合物包括選自由 肆(2,2,2·:氟乙氧基㈣燒,肆(三氟乙龜氧基)_燒,四異 氯酸醋基珍燒、參(2,2,2-三氟乙氧基)甲基矽烷,參(三氟 乙醯氧基)甲基矽烷、曱基三異氰酸酯基矽烷及其結合物 組成之群組之含矽預聚物。 17. 如申請專利範圍第丨項之方法,其中成孔劑之滞點、昇華 點或分解溫度為約150°C至約450°C。 18. 如申請專利範圍第”貝之方法,其中步驟⑷之交聯係在溫 度低於步騾(d)之加熱溫度下進行。 19·如申請專利範圍第之方法,其中步驟⑷包括使薄膜在 溫度約lOOt:至約25(TC下加熱約30秒至約1〇分鐘。 20.如申請專利範圍第!項之方法,其中步驟⑷包括使薄膜在 約150 C至約450 C之溫度下加熱約30秒鐘至約1小時。 21·如申請專利範圍第1項之方法,其中成孔劑之分子量約 100 至約 50,000 amu。 22·如申请專利範圍第1項之方法’其中該成孔劑係選自由聚 環氧烷、聚環氧烷之單醚、聚環氧烷之二_、聚環氧、燒 之雙氣甲醚(bisether)、脂系聚酯、丙晞酸系聚合物、乙縮 酸聚合物、聚(己内酯)、聚(戊内酯)、聚(甲基丙烯酸甲 酯)、聚(乙烯基丁醛)及其結合物組成之群組。 23·如申請專利範圍第1項之方法,其中該成孔劑包括聚環氧 84564 200403764 烷單醚,其在氧原子及^至約Q烷基醚基團間包含C!至約 C6燒基鏈’且其中之烷基鏈為經取代或未經取代。 24. 如申请專利範圍第23項之方法,其中該聚環氧烷單醚為 聚乙二醇單甲基醚或聚丙二醇單丁基醚。 25. 如申請專利範圍第丨項之方法,其中該成孔劑在組合物中 之含里為組合物之約1至約5〇wt% 〇 26. 如申請專利範圍第巧之方法,其中該組合物尚包括溶劑。 27. 如申請專利範圍第丨項之方法,其中該组合物尚包括溶劑84564 200403764 Non-metallic and nucleophilic additives that crosslink the composition. 9. The method according to item 1 of the patent application scope, wherein the composition further comprises a nucleophilic additive that can accelerate the crosslinking of the composition, and the additive is selected from the group consisting of dimethyl block, dimethyl methylamine, and hexamethyl Phosphorus triamine, group of amines and combinations thereof. 10. The method of claim 1, wherein the composition further comprises water, and the molar ratio of water to Si is about 0.1: 1 to about 50: 1. U. The method of claim 1, wherein the composition includes a silicon-containing prepolymer of formula I: Rx-Si-Ly (formula I) where X is an integer from 0 to about 2, and y is 4 Χ (an integer from about 2 to about 4); R is independently selected from the group consisting of alkyl, aryl, hydrogen, alkylene, aryl, and combinations thereof; L is a negatively charged group, which is Independently selected from the group consisting of an alkoxy group, a carboxyl group, an ethoxyl group, an amine group, a sulfonium group, a compound, an isocyanate group, and a combination thereof. 12. The method of claim n of claim 1, wherein the composition comprises a polymer formed by condensing a prepolymer of formula I, wherein the number average molecular weight of the polymer is from about 150 to about 300,000. amu. 13. The method according to item 1 of the patent application range, wherein the composition comprises a silicon-containing prepolymer selected from the group consisting of ethoxylated oxalate, ethoxysilane, methoxysilane, and combinations thereof. 14. The method of claim i, wherein the composition comprises a composition selected from the group consisting of tetraethoxysilane, Ci to about c6 alkyl or aryl-triethoxysilane 84564 200403764 and combinations thereof Group of sand-containing prepolymers. 15. For example, the method of claim 14 of the scope of patent application, in which the triethoxysilane is methyl triethyl donkey oxide crushed. 16. The method as claimed in the patent application, wherein the composition comprises a compound selected from the group consisting of (2,2,2 ·: fluoroethoxy stilbene, tris (trifluoroethylpyroxy)), tetraisochloroacetate The group consisting of Jizhenyan, ginseng (2,2,2-trifluoroethoxy) methylsilane, ginseng (trifluoroethoxy) methylsilane, fluorenyl triisocyanate silane and combinations thereof Silicon-containing prepolymer. 17. The method according to item 丨 of the patent application, wherein the stagnation point, sublimation point, or decomposition temperature of the pore-forming agent is about 150 ° C to about 450 ° C. The method in which step 联系 is performed at a temperature lower than the heating temperature of step 骡 (d). 19. The method according to the scope of the patent application, wherein step ⑷ includes bringing the film at a temperature of about 100 t: to about 25 ( Heating at TC for about 30 seconds to about 10 minutes. 20. The method according to item No. of the patent application, wherein step ⑷ includes heating the film at a temperature of about 150 C to about 450 C for about 30 seconds to about 1 hour. 21. The method according to item 1 of the patent application scope, wherein the molecular weight of the pore-forming agent is about 100 to about 50,000 amu. The method of the first item of the scope of interest 'wherein the pore-forming agent is selected from the group consisting of polyalkylene oxide, a monoether of polyalkylene oxide, two of polyalkylene oxide, polyepoxide, and bisether. , Fatty polyester, propionic acid polymer, acetic acid polymer, poly (caprolactone), poly (valerolactone), poly (methyl methacrylate), poly (vinyl butyral) and The group consisting of combinations thereof. 23. The method according to item 1 of the patent application range, wherein the pore former comprises polyepoxy 84564 200403764 alkyl monoether, which is between an oxygen atom and ^ to about Q alkyl ether groups Containing C! To about C6 alkyl groups, and wherein the alkyl chain is substituted or unsubstituted. 24. The method according to item 23 of the patent application, wherein the polyalkylene oxide monoether is a polyethylene glycol monoether Methyl ether or polypropylene glycol monobutyl ether. 25. The method of claim 丨, wherein the content of the pore-forming agent in the composition is about 1 to about 50 wt% of the composition. 26. For example, the method of claiming a patent scope, wherein the composition further comprises a solvent. 27. For example, the method of claiming a patent scope, wherein the composition Solvent included ’其量為組合物之約10至約95wt〇/〇。 28. 如申請專利範圍第α之方法,其中該組合物尚包括滞點 約50至約25(TC之溶劑。 29. 如申請專利範圍第巧之方法,其中該組合物尚包括選自 由烴、醋、靆、酮、醇、醯胺及其結合物組成之群組之 溶劑。&Apos; Its amount is from about 10 to about 95 wt% of the composition. 28. The method according to the patent application No. α, wherein the composition still includes a solvent having a stagnation point of about 50 to about 25 ° C. 29. The method according to the patent application, wherein the composition further includes a solvent selected from the group consisting of hydrocarbons, Solvents in the group consisting of vinegar, acetone, ketone, alcohol, amidine and combinations thereof. 30. 如申請專利範圍第26項之方法,其中該溶劑係選自由二 正丁基鍵、苯甲醚、丙酮、3_戊酮、2_庚酮、乙酸乙酉旨、 乙酸正丙酯、乙酸正丁酯、乳酸乙酯、乙醇、2_丙醇、 :甲基乙醯胺、丙二醇曱基醚乙酸酯及其結合物組成之 31. 一種奈米多孔性介電質薄膜 第1項之方法在基材上形成。 其係藉由如申請專利範圍 32. 一種半導體裝置, 多孔性介電質薄膜 其包括如申凊專利範圍第31項之奈米 其為積體電路。 33·如_請專利範圍第32項之半導體裝置 84564 200403764 34· —種組合物,其包括含碎之預聚物、成孔劑及選自 化合物及親核物組成之群組之觸媒。 35·如申請專利範圍第34項之組合物,其中該觸媒不含Α 離子。 36·如申請專利範圍第34項之組合物,其可額外包含溶劑。 37.如申請專利範圍第35項之組合物,其中該不含金屬離予 之觸媒為乙酸四甲基銨。 38·如申請專利範圍第34項之組合物,其中該含矽預聚物~ 括以乙醯氧基為主之離去基之結合物。 39_如申請專利範圍第%項之組合物,其中該以乙驢氧美為 主之離去基之結合物包括四乙酸氧基石夕燒及甲其= 忍二乙酿 氧基矽烷。 40·如申請專利範圍第34項之組合物,其中該成孔劑包括产 乙二醇單甲基醚。 a 41·如申請專利範圍第34項之組合物,其中該成孔劑包括严 丙二醇二甲基醚。 &quot; 42·如申請專利範圍第34項之組合物,其中該成孔劑包括聚 乙二醇二甲基醚。 水 43.如申請專利範圍第34項之組合物,其中該成孔劑包括聚 丙二醇單丁基醚。 ^ 44· 一種用於穩定奈米多孔性薄膜形成之前驅物,其包括如 申请專利範圍第35項之組合物。 45· —種旋轉塗佈用組合物,其包括如申請專利範圍第%項 之組合物。 84564 200403764 46. 種薄膜,其包括如申請春丨 μ 組合物。 專]靶圍罘45項之旋轉塗佈用 47· 一種穩定之奈米多孔性薄 仆八仏π、 涛膜包括矽聚合物及選自由鏘 化占物及親核物組成之群扣 4〇 4 ^ , 风艾鮮組^不含金屬離子之觸媒。 48·如申請專利範圍第47項 杨疋奈未多孔性薄膜,其中該 薄膜&lt;平均孔隙直徑小於或等於約10奈米。 49·如申請專利範圍第47項 _ /、 釔疋丁、未多孔性薄膜,其中該 溥膜之平均孔隙直徑小於或等於約5奈米。 50·如申請專利範圍第47項凌藉令太止# 导_牟/貝疋%疋奈未多孔性薄膜,其中該 不含金屬離子之觸媒為乙酸四甲基銨。 5!.如申請專利範圍第47項之穩定奈米多孔性薄膜,其中該 含石夕I預聚物包括以乙醯氧基為主之離去基之結合物。 52·如中請專利範圍第47項之穩定奈米多孔性薄膜,其中該 以乙醯氧基為王之離去基之結合物包括四乙醯氧基矽烷 及甲基三乙酸氧基碎垸。 53. —種使形成多孔性矽石薄膜之溫度降低之方法,包括之 步驟為將鑌離子或親核物添加於含矽之預聚物及成孔劑 中0 84564 6-30. The method of claim 26, wherein the solvent is selected from the group consisting of a di-n-butyl bond, anisole, acetone, 3-pentanone, 2-heptanone, ethyl acetate, n-propyl acetate, n-butyl acetate Ester, ethyl lactate, ethanol, 2-propanol,: methylacetamide, propylene glycol ethyl ether acetate, and combinations thereof 31. A method of nanoporous dielectric film in item 1 is Formed on the substrate. It is as described in the patent application scope 32. A semiconductor device, a porous dielectric film, which includes nanometers as described in the patent application scope item 31, which is an integrated circuit. 33. For example, please refer to the semiconductor device of item 32 of the patent. 84564 200403764 34. A composition comprising a prepolymer containing pulverization, a porogen, and a catalyst selected from the group consisting of a compound and a nucleophile. 35. The composition of claim 34, wherein the catalyst does not contain A ions. 36. The composition of claim 34, which may additionally include a solvent. 37. The composition of claim 35, wherein the metal-free catalyst is tetramethylammonium acetate. 38. The composition of claim 34, wherein the silicon-containing prepolymer includes a combination of a leaving group mainly composed of ethoxyl. 39_ The composition according to item% of the scope of patent application, wherein the combination consisting of ethoxybenzyl as the main leaving group includes tetraacetoxy oxalate and melamine = diethylene glycol oxysilane. 40. The composition of claim 34, wherein the pore former comprises ethylene glycol monomethyl ether. a 41. The composition of claim 34, wherein the pore former comprises propylene glycol dimethyl ether. &quot; 42. The composition according to claim 34, wherein the pore former comprises polyethylene glycol dimethyl ether. Water 43. The composition of claim 34, wherein the pore former comprises polypropylene glycol monobutyl ether. ^ 44. A precursor for stabilizing a nanoporous film, comprising a composition such as the 35th item in the patent application. 45 · A composition for spin coating, which includes a composition such as item% of the scope of patent application. 84564 200403764 46. A film comprising a composition as described in the application spring. [Special] Target coating of 45 items for spin coating 47. A stable nanoporous thin thin film 仏 仏, the membrane includes silicon polymer and is selected from the group consisting of tritiated compounds and nucleophiles 4〇 4 ^, Feng Aixin Formation ^ does not contain metal ion catalyst. 48. According to item 47 of the scope of application for a patent, Yang Minai's non-porous film, wherein the film &lt; average pore diameter is less than or equal to about 10 nm. 49. For example, the scope of the application for patent No. 47 _ /, yttrium tintin, non-porous thin film, wherein the average pore diameter of the hafnium film is less than or equal to about 5 nm. 50. For example, the scope of patent application No. 47 Ling Borrow Order Taizhi # 导 _ 牟 / 贝 疋% 疋 奈 non-porous film, wherein the metal ion-free catalyst is tetramethylammonium acetate. 5 !. The stabilized nanoporous film according to item 47 of the application, wherein the Shixi I-containing prepolymer includes a combination of a leaving group mainly composed of ethoxyl. 52. The stabilized nanoporous film according to item 47 of the Chinese Patent Application, wherein the combination of acetylacetoxy as the leaving group includes tetraethoxysilane and methyltriacetoxyacetate. . 53. —A method for reducing the temperature of forming a porous silica film, including the step of adding a europium ion or a nucleophile to a silicon-containing prepolymer and a pore former 0 84564 6-
TW092108111A 2002-04-10 2003-04-09 Low metal porous silica dielectric for integral circuit applications TW200403764A (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US37165402P 2002-04-10 2002-04-10
PCT/US2002/015256 WO2003088344A1 (en) 2002-04-10 2002-04-10 Low metal porous silica dielectric for integral circuit applications

Publications (1)

Publication Number Publication Date
TW200403764A true TW200403764A (en) 2004-03-01

Family

ID=52340025

Family Applications (1)

Application Number Title Priority Date Filing Date
TW092108111A TW200403764A (en) 2002-04-10 2003-04-09 Low metal porous silica dielectric for integral circuit applications

Country Status (1)

Country Link
TW (1) TW200403764A (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7389122B2 (en) 2004-12-17 2008-06-17 Intel Corporation Method and apparatus to provide a continuous useable wireless network connection

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7389122B2 (en) 2004-12-17 2008-06-17 Intel Corporation Method and apparatus to provide a continuous useable wireless network connection

Similar Documents

Publication Publication Date Title
US7381441B2 (en) Low metal porous silica dielectric for integral circuit applications
JP4125637B2 (en) Low dielectric constant material and manufacturing method thereof
TWI299321B (en) Low dielectric materials and methods for making the same
JP4874614B2 (en) Porous low dielectric constant compositions and methods for making and using the same
TWI275106B (en) Compositions for preparing low dielectric materials containing solvents
TWI284140B (en) Method for forming porous silica film
JP2006500769A (en) Interlayer adhesion promoter for low-k materials
US7381442B2 (en) Porogens for porous silica dielectric for integral circuit applications
US6015457A (en) Stable inorganic polymers
WO2007142000A1 (en) Precursor composition for porous membrane, process for preparation of the precursor composition, porous membrane, process for production of the porous membrane, and semiconductor device
KR20110021951A (en) Method of making porous materials and porous materials prepared thereof
WO2004026765A1 (en) Method for modifying porous film, modified porous film and use of same
WO2008026387A1 (en) Method of forming amorphous silica coating of low dielectric constant and amorphous silica coating of low dielectric constant obtained thereby
EP1412434A1 (en) Siloxane resins
JP4261297B2 (en) Method for modifying porous film, modified porous film and use thereof
JP2004210579A (en) Method of producing porous silica film, porous silica film obtained by the method, and semiconductor device made of the same
JP2012104616A (en) Precursor composition of low dielectric constant film and method for manufacturing low dielectric constant film using the same
TW200403764A (en) Low metal porous silica dielectric for integral circuit applications
KR20050016505A (en) Organosiloxanes
JP6042151B2 (en) Insulating material for semiconductor containing silica particles
JP3883174B2 (en) Semiconductor substrate with low dielectric constant silica-based coating and method of forming low dielectric constant silica-based coating
JP2005116830A (en) Porous silica, manufacturing method thereof and application thereof
KR20000004971A (en) Coating solution for forming silica film having low dielectric constant and substrate applied with the film
TW200306282A (en) New porogens for porous silica dielectric for integral circuit applications
JP2011040634A (en) Precursor composition of porous film, porous film, method of manufacturing the same, and semiconductor device