本研究以大量廢磚粉、廢陶瓷粉為原料，以廢陶瓷砂為細粒料，在常溫條件下養護，製作鹼激發漿體和砂漿。採用水淬高爐石粉（GGBFS）和燃煤飛灰（FA）對WBP和WCP進行調整。以Na2SiO3和NaOH溶液為鹼激發液體。本研究主要分為三個部分。在研究的第一部分中，製備了高强度鹼激發漿體（AAP），使WBP和WCP約占原材料總重量的60%。其次，採用GGBFS代替WBP和WCP，以0～50%的重量比對鹼激發砂漿（AAM）的效能進行了評估。最後，研究了鹼激發劑濃度和細粒料種類對WBP基AAM的影響。Na2O含量在2～10%之間，SiO2/Na2O比值在0.25～2之間，而NFA、RFA和WCS則以不同比例作為細粒料。通過新拌性質（坍落度、凝結時間）、硬固性質（抗壓強度、密度、超音波波速（UPV）、熱導率（TC）和顯微結構，採用X射線繞射（XRD）、掃描電子顯微鏡（SEM）和能譜儀（EDS）對AAP和AAM的效能進行了測試，熱重分析（TGA）和傅立葉轉換紅外光譜（FTIR） 。硬化後的AAP試樣在36-70 MPa範圍內獲得了較高的抗壓強度。採用100% WBP和WCP製備AAM，在不同鹼激發劑濃度下室溫養護下皆不成功。當WBP和WCP與GGBFS從10% 重量比開始混合時，AAM被成功地開發出來。隨著GGBFS含量的增加和養護齡期的延長，AAM的强度提高，顯微組織改善。此外，在室溫下，使用濃度為4% Na2O和0.5 SiO2/Na2O的鹼激發劑可以有效地製備AAM。總而言之，隨著GGBFS含量和鹼激發劑濃度的增加，AAP和AAM表現出更佳的力學和微觀結構性質，並呈現出明顯的改善趨勢。XRD分析顯示，所有混合物的主要鹼激發反應產物為CSH、CASH和NASH膠體，而石英（SiO2）為主要的晶相。隨著GGBFS和鹼激發劑濃度的新增，膠體基質的緻密程度明顯提高。WCS部分取代NFA達50%，可使AAM的抗壓強度提高16%。本研究進一步證明了在室溫養護條件下，大量使用WBP、WCP和WCS開發AAP和AAM的强大潜力。

The main aim of this study was to develop alkali activator paste and mortar by using a high volume of waste brick powder (WBP) and Waste ceramic powder (WCP) as starting materials and waste ceramic sand (WCS) as fine aggregate material cured under ambient temperature condition. Ground granulated blast furnace slag (GGBFS) and fly ash (FA) were used to modify WBP and WCP precursors. A combination of Na2SiO3 and NaOH solutions were used as alkali activator liquid. The study can be categorized into three main parts. In the first part, high strength alkali-activated paste (AAP) was prepared in such a way that WBP and WCP comprised about 60% of the total weight of the starting materials. Secondly, the performance of alkali-activated mortar (AAM) was evaluated by using GGBFS to replace WBP and WCP from 0 to 50% by weight. Lastly, the effect of alkali activator concentration and fine aggregate types on WBP based AAM was investigated. Na2O content was used between 2 and 10% and the SiO2/Na2O ratio varying between 0.25 and 2 while NFA, RFA, and WCS were used in different proportions as fine aggregate materials. The performance of AAP and AAM was examined through the fresh properties (slump flow, setting time), the hardened properties (compressive strength, density, ultrasonic pulse velocity (UPV), thermal conductivity (TC) and the microstructure by X-ray diffraction (XRD), Scanning electron microscopy (SEM) with energy dispersive spectrometer (EDS), thermogravimetric analysis (TGA) and Fourier transform infrared spectroscopy (FTIR). The hardened AAP samples obtained high compressive strength results measured in the range of 36–70 MPa. The development of AAM with 100% WBP and WCP was not successful in different alkali activator concentrations. AAM was successfully developed when WBP and WCP were blended with GGBFS starting from 10% by weight. The strength improved and microstructure of AAM improved with higher inclusion of GGBFS content and curing age. Moreover, AAM mixtures were effectively developed at ambient-temperature curing using concentrations of alkali activators (starting from 4% Na2O and 0.5 SiO2/Na2O ratio). In general, AAP and AAM showed excellent mechanical and microstructure properties displaying a trend improvement with increasing in GGBFS content and alkali activator concentration. The XRD analysis revealed that the main alkali activation reaction products of all mixtures to be C-S-H, C-A-S-H and N-A-S-H gels while quartz (SiO2) was found to be the major crystalline phase. The densification of the gel matrix was significantly improved with increasing GGBFS and alkali activator concentration. The partial replacement of NFA by WCS up to 50% by weight enhanced the compressive strength of AAM up to 16%. This study further demonstrates the strong potential of using WBP, WCP, and WCS on a high volume basis for the development of AAP & AAM through ambient temperature curing conditions.

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