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Reaction Densification of -SiAION: II, Densification Behavior
-SiAION的反应 致密化：II，致密化行为

Mohan Menon and I-Wei Chen*
莫汉·梅农（Mohan Menon）和陈怡薇（I-Wei Chen）*Department of Materials Science and Engineering, University of Michigan, Ann Arbor, Michigan 48109-2136
密歇根大学材料科学与工程系， 密歇根州安娜堡 48109-2136

Reaction hot-pressing behavior of , and powder mixtures , Dy, Er, and Yb) forming -SiAION has been studied. Five characteristic temperatures are found to control the densification behavior of these materials. The densification proceeded in three major stages. The first two stages were formation of ternary oxide eutectic and wetting of majority nitride powder. The third stage involved dissolution/melting of intermediate phase. Variation from this behavior sometimes occurs due to localization of wetting liquid at AIN, extremely high melting/dissolution temperature of and and melilite, and secondary precipitation of Dy- -SiAION. The dominant densification mechanism was found to be massive particle rearrangement, irrespective of the wetting and dissolution/melting behavior. The efficiency of this mechanism is mostly affected by the amount of available liquid and less by its viscosity. Fully dense, single-phase ceramics were obtained in all cases except Mg when hot-pressed at a constant heating rate to , and considerably lower temperatures for , Gd, Dy, Er, and Yb-SiAION when held isothermally.
研究了 与 粉末混合物 、Dy、Er和Yb）形成 -SiAION的反应热压行为。发现五种特征温度可以控制这些材料的致密化行为。致密化分三个主要阶段进行。前两个阶段是三元氧化物共晶的形成和多数氮化物粉末的润湿。第三阶段涉及中间相的溶解/熔化。这种行为的变化有时是由于润湿液在AIN的局部化， 和 和 和melilite的极高熔化/溶解温度 ，以及Dy- -SiAION的二次沉淀。主要的致密化机制是大量的颗粒重排，而与润湿和溶解/熔融行为无关。这种机制的效率主要受可用液体量的影响，而受其粘度的影响较小。在所有情况下，除了以恒定加热速率热压至 Mg时，以及当保持等温时 ，Gd、Dy、Er和Yb-SiAION的温度要低得多，因此在所有情况下都获得了全致密的单相陶瓷。

I. Introduction 一、引言

S INCE the concept of "transient liquid sintering" was introduced, intensive investigations have been done on the reaction sintering of SiAION in the metal oxide- system. Some of the earliest work was carried out in the system by Lewis et al. They found that a transient phase which formed during the hotpressing of with reacted with above to form and a vitreous phase. This reaction was found to expedite the sintering kinetics. Further, they found that the sintering kinetics and the reaction pathway of a mixture of depended on the amount of The addition of , instead of to a mixture resulted in a sample with diphasic SiAION (YAG) microstructure with improved mechanical properties. Boskovic al. used the concept of transient liquid sintering to obtain dense -SiAlON ceramics in the plane. In their study, they too found that the sintering kinetics depended on the composition of starting powder mixtures, even though the final composition was the same. In these and other reaction hot-pressing studies, the densification mechanisms were identified to be either solution-reprecipitation, fast particle rearrangement, Coble creep, or grain boundary sliding. 9,11
引入了“瞬态液体烧结”的概念，对SiAION在金属氧化 物 体系中的反应烧结进行了深入研究。 一些最早的工作是由Lewis等人在 系统中进行的。 他们发现，在 热压过程中形成的瞬态相与 上面 的玻璃 相反应形成。 发现该反应可以加速烧结动力学。此外，他们发现，混合物的烧结动力学和反应途径 取决于 添加量，而不是 添加到 混合物中，从而使样品具有具有改进的机械性能的双相 SiAION （YAG）微观结构。 Boskovic 等人使用瞬态液体烧结的概念在 平面上获得了致密 的-SiAlON陶瓷。 在他们的研究中，他们也发现烧结动力学取决于起始粉末混合物的成分，即使最终成分相同。在这些和其他反应热压研究中，致密化机制被确定为溶液再沉淀、 快速颗粒重排、 Coble 蠕变 或晶界滑动。9,11
Recently, Hwang and Chen found that reaction hot pressing of and -SiAlON took place in three stages. Further, they found that the wetting properties of the eutectic melt controlled the densification behavior of the powder compact. The first stage was identified with the
最近，Hwang和Chen发现 和 -SiAlON的反应热压分三个阶段进行。 此外，他们发现 共晶熔体的润湿性能 控制了粉末压块的致密化行为。第一阶段被确定为
formation of the ternary oxide eutectic and YAG. The shrinkage in this stage was due to the redistribution of liquid in the powder compact and slight improvement in the packing efficiency. The second stage was identified with the wetting of AIN particles and formation of . The preferential wetting of AlN by the ternary oxide melt caused localization of the liquid, leading to a delaying effect on the second shrinkage step. The third stage occurred with the dissolution of and formation of the final phase. Massive particle rearrangement was found to be the dominant densification mechanism. It also caused enrichment in the liquid, leading to formation of as a transient phase. Thus the physical/chemical characteristics of the liquid, in particular its wetting behavior, and the kinetic pathway of the intermediate reactions are clearly important factors in reaction densification of multicomponent systems.
三元氧化物共晶和YAG的形成。这一阶段的收缩是由于液体在粉末压实中的重新分布和包装效率的略有提高。第二阶段是AIN颗粒的润湿和形成 。三元氧化物熔体对AlN的优先润湿导致液体局部化，导致第二收缩步骤的延迟效应。第三阶段随着最后阶段的 解散和形成而发生。发现大量颗粒重排是主要的致密化机制。它还导致 液体富集，导致 形成瞬态相。因此，液体的物理/化学特性，特别是其润湿行为，以及中间反应的动力学途径显然是多组分体系反应致密化的重要因素。
The preceding paper (part I) has provided a broad picture of the wetting behavior of the ternary oxides and reaction pathways in the system , Dy, Er, and Yb). Generally, the more basic oxides wet , whereas the more acidic oxides wet AIN. It has also identified temperatures for the various reactions which can be used to
前面的论文（第一部分） 提供了三元氧化物的润湿行为和反应途径在 体系 中，Dy、Er和Yb的润湿行为。 一般来说，碱性氧化物越多 ，而酸性氧化物就越湿。它还确定了可用于
(a)
(b)
Fig. 1. Schematic shrinkage curves when the eutectic melt wets (a) , and (b) AIN first.
图 1.共晶熔体先润湿（a） 和（b）AIN时的收缩曲线示意图。
Manuscript No. 193383. Received August 3, 1994; approved October 17, 1994 Supported by the National Science Foundation under Grant No. DDM-9024975. "Member, American Ceramic Society.
手稿编号 193383.收稿日期： 1994-08-03;1994 年 10 月 17 日批准 由美国国家科学基金会资助，资助号为DDM-9024975 中。“美国陶瓷学会会员。
understand the shrinkage behavior. The reactions identified during the reaction densification of -SiAlON are (i) the eutectic formation (at temperature ), (ii) wetting of a nitride powder and intermediate phase precipitation (at temperature ), (iii) secondary wetting of the other nitride powder (at temperature ), (iv) dissolution of the intermediate phase (at temperature ), and (v) precipitation of the final phase, -SiAION (at temperature ). Figures and (b) show the schematic of expected shrinkage curves when the eutectic melt preferentially wets and , respectively. In these curves, the beginning of various shrinkage steps are identified with some of the above characteristic temperatures. Wetting of AIN is shown to lead to small or no immediate shrinkage in the powder compact because of the low AIN content of the typical SiAION compact. In Fig. 1(b), though, a subsequent shrinkage step occurs when the majority is wetted. Variation of these shrinkage curves may also be possible. For example, it is known that the initial precipitation of the intermediate phase usually starts with partial wetting of the first nitride; i.e., could be significantly lower than the temperature when complete wetting is achieved. Also, the dissolution of intermediate phase may or may not precede the precipitation of -SiAlON; i.e., may or may not be higher than . Indeed may even be lower than , as shown later.
了解收缩行为。 在-SiAlON反应致密化过程中确定的反应是（i）共晶形成（在温度 下），（ii）氮化物粉末的润湿和中间相沉淀（在温度 下），（iii）其他氮化物粉末的二次润湿（在温度 下），（iv）中间相的溶解（在温度 下），以及（v）末相 -SiAION的沉淀（在温度 下）。 图 和（b）分别显示了共晶熔体优先润湿 时的预期收缩曲线示意图。在这些曲线中，各种收缩步骤的开始被识别为上述一些特征温度。由于典型SiAION压块的AIN含量低，AIN的润湿会导致粉末压块的微小收缩或没有立即收缩。 然而，在图1（b）中，当大部分 被润湿时，会发生随后的收缩步骤。这些收缩曲线的变化也是可能的。例如，众所周知，中间相的初始沉淀通常从第一氮化物的部分润湿开始;即， 当实现完全润湿时，温度可能明显低于温度。 此外，中间相的溶解可能先于 -SiAlON沉淀，也可能不先于-SiAlON沉淀; 即， 可能高于 ，也可能不高于 。事实上 甚至可能低于 ，如后所示。
In this paper, we report the densification behavior during the reaction hot pressing of -SiAlON system with metal oxide additions . Hot pressing was applied to provide a constant driving force for densification. The characteristic temperatures discussed above are identified for various systems using shrinkage data and information from part I. The role of wetting behavior of the ternary oxide melt and the formation/dissolution of intermediate phases in densification is then assessed along with other kinetic considerations such as amount and viscosity of the liquid. Some general conclusions are drawn from these comparisons to further our understanding of reaction densification of these complex systems.
本文报道了 -SiAlON体系与金属氧化物添加反应热压过程中的致密化行为 。采用热压为致密化提供恒定的驱动力。上面讨论的特征温度是使用收缩数据和第一部分的信息为各种系统确定的。然后评估三元氧化物熔体的润湿行为和中间相的形成/溶解在致密化中的作用以及其他动力学考虑因素，例如液体的量和粘度。从这些比较中得出了一些一般结论，以进一步理解这些复杂系统的反应致密化。

II. Experimental Procedure
二、实验程序

(1) Composition （1）组成

The compositions investigated lie on the so-called -plane represented by the formula . Specifically, , and and (1210) were chosen because they lie inside the single-phase region. The compositions studied are listed in Table I and are the same as reported in part I.
所研究的成分位于由公式 表示的所谓 -平面上。具体来说， 选择 和 和 （1210） 是因为它们位于单相 区域内。所研究的成分列于表一中，与第一部分报告的成分相同。

(2) Powder Preparation and Hot Pressing
（2）粉末制备和热压

Details of powder preparation and hot pressing are given in part I. Hot-pressing data reported here were obtained from runs at a constant heating rate of to in most cases. The temperature when full density is obtained during the above runs is denoted as . Isothermal runs held at some intermediate temperatures were also performed to approximately locate the lowest temperature, denoted by , required to obtain full density. In addition, densification kinetics were evaluated during isothermal hold for some systems.
粉末制备和热压的细节在第一部分中给出， 这里报告的热压数据是在大多数情况下从恒定加热速率 到的 运行中获得的。在上述运行过程中获得全密度时的温度表示为 。还进行了在一些中间温度下保持的等温运行，以大致定位获得全密度所需的最低温度，用 表示。此外，还评估了某些系统在等温保持期间的致密化动力学。
Table I. Compositions Studied (wt%)
表I. 研究的成分（wt%）
Material Additive AlN
Li 1010 2.63 2.99 12.03 82.35
4.83 2.92 11.76
Mg 1010 3.52 2.96 11.92 81.60
Y 1010 6.37 2.88 11.57 79.18
Nd 1210 10.88 2.20 12.82 74.10
Sm 1210 11.24 2.19 12.76 73.81
Gd 1210 11.63 2.18 12.70 73.49
Dy 1210 11.93 2.17 12.66 73.24
12.20 2.16 12.62 73.02
Yb 1210 12.52 2.15 12.58 72.75

III. Results 三、结果

A summary of the densification behavior is given in Tables II and III. Table II gives the characteristic temperatures, , along with the volume shrinkage for the first two steps. Table III gives the two densification temperatures to reach full density, and , as well as the phase assemblages at . The phase assemblages at are already given in Table II of part for most of the systems.
致密化行为的摘要见表二和表三。表II给出了特性温度， 以及前两个步骤的体积收缩率。表III给出了达到全密度的两个致密化温度， 以及 的 相组合。对于大多数系统，部分 的相位组合 已经在表II中给出。

(1) Alkali and Alkaline-Earth Oxides
（1）碱土氧化物

The systems studied here were M-1010, M being Li, Ca, and .
这里研究的系统是M-1010，M是Li，Ca和 .
(A) Li System: The shrinkage of the Li-1010 sample contains three well-defined stages (Fig. 2(a)). The first shrinkage step occurs at accompanied by shrinkage. The second step occurs at , accompanied by shrinkage. The third step occurs at . A fourth step occurs at . Full density is achieved at under constant heating rate and can also be achieved at when held over .
（A） Li System：Li-1010 样品的收缩包含三个明确定义的阶段（图 2（a））。第一个收缩步骤发生在 伴随着 收缩。第二步发生在 ，并伴有 收缩。第三步发生在 。第四步发生在 。在恒定的加热速率 下可实现全密度，也可以在 保持时 实现。
For this system, in which wetting of is preferred and is complete at the characteristic temperatures are and , corresponding to the formation of oxide melt, and the wetting of , respectively. The third shrinkage step starting at seems to correspond to the dissolution of the intermediate phase , hence at . Since formation was detected above , according to part yet AlN still remained at after isothermal hold but not at the step at is possibly related to wetting and dissolution of .
对于该系统，其中润湿 是优选的，并且在 特征温度下 完全是 和 ，分别对应于氧化物熔体的形成和 的润湿。从 开始 的第三个收缩步骤似乎对应于中间相 的溶解，因此在 。由于 上面 检测到了地层，因此部分 AlN 在等温保持后仍保持在等温保持处，但在步骤中 仍 未保持，这可能与润 湿和溶解有关。
(B) Ca System: Compared to Li-1010, the shrinkage curve of Ca-1010 has fewer well-separated steps (Fig. 2(b)). However, on closer examination, three shrinkage steps can be identified. The first shrinkage step occurs at . A second step is identified around , followed by continuous gradual shrinkage. A third step at and another at seem to be present. Full density can be achieved at under constant heating rate and also at when held for . Full densification was not possible at .
（B）钙体系：与Li-1010相比，Ca-1010的收缩曲线具有较少的分离步骤（图2（b））。然而，经过仔细检查，可以确定三个收缩步骤。第一个收缩步骤发生在 。第二步被确定为， 然后是连续的逐渐收缩。第三步似乎 存在，另一步似乎 存在。 在恒定的加热速率下可以实现全密度，也可以 在保持时 实现。在 处不可能完全致密化。
For this system, in which is preferentially and completely wetted at , we can identify and . They correspond to the formation of eutectic and wetting of , respectively, like the system. The third shrinkage step again appears to be due to the dissolution of . Lastly, since some already has formed at and AIN remains at after isothermal hold, the step at is possibly due to AlN wetting and dissolution .
对于这个系统，其中 优先和完全润湿， 我们可以识别 和 。它们分别对应于 共晶和润湿的形成，就像 系统一样。第三个收缩步骤似乎是由于 的溶解 。最后，由于一些 已经在等 温保持后形成，而AIN保持在等温保持 后， 步骤可能是 由于AlN润湿和溶解 。
(C) Mg System: Mg-1010 was found to be very difficult to densify. Under constant heating conditions only dense samples were obtained at . Distinct shrinkage steps can easily be identified (Fig. 2(c)). One distinct step occurs at , although a smaller step at seems also discernible. Another distinct step was found at . Although a number of additional shrinkage steps, whose positions were found to vary from run to run, exist between and , densification is sluggish. The origin of this sluggish densification is the formation of a highly refractory following wetting of This compound does not melt even at and it deprives the compact of the sintering liquid.
（C）镁系统：发现Mg-1010很难致密化。在恒定加热条件下，仅 获得致 密样品。可以很容易地识别出不同的收缩步骤（图2（c））。一个明显的步骤出现在 ，尽管似乎也可以看出一个较小的步骤 。在 中发现了另一个明显的步骤。尽管在 和 之间存在着许多额外的收缩步骤，其位置因运行而异，但致密化是缓慢的。这种缓慢致密化的起源是在润 湿 后形成高度难熔的化合物，即使在 AT 时也不会熔化 ，并且它剥夺了烧结液的压实物。
The characteristic temperatures identified for this system are as follows: corresponding to formation of eutectic and corresponding to wetting and formation of . In addition, the step at is very likely due to AlN wetting, hence . The steps at higher temperatures vary in position, probably because of the heterogeneous nature of the very slow reaction of AIN in the presence of the small amount of liquid. The dissolution temperature of the intermediate phase is very high while the formation temperature of is .
该系统确定的特征温度如下： 对应于共晶的形成和对 应于 润湿和形成 。此外，阶跃很可能是 由于 AlN 润湿造成的，因此 .较高温度下的步骤位置不同，可能是因为在少量液体存在下，AIN反应非常缓慢的异质性。中间相的溶解温度非常高， 而中间相的 形成温度为 。

(2) Rare Earths （2）稀土

The shrinkage curves of these materials are shown in Figs. 3-6, all hot pressed to . Under constant heating
这些材料的收缩曲线如图3-6所示，全部热压至 。在恒定加热下
Table II. Summary of Features of the Shrinkage Curves for Samples Hot Pressed at a Heating Rate of
表二.以
System Volume shrinkage
体积收缩
First stage Second stage
1010 1225 1600 1500 1420 8.0 15.0
1360 1450 1660 1610 1550 5.0 28.0
1350 1500 1630 1575 5.0 9.0
1400 1450 1580 1420 4.0 15.0
1380 1460 1600 1420 7.0 17.0
Gd 1370 1500 1620 1700 1575 7.0 10.0
Dy 1360 1560 5.0 20
1400 1580 1640 1580 4.0 13.0
1380 1560 1640 1560 9.0 10.0
Table III. Lowest Temperature to Reach Full Density under Constant Heating Rate ) or under Isothermal Hold ( )
表三.在恒定加热速率 下达到全密度的最低温度）或等温保持（ ）
System at time Phase assemblage at
相 位组装
, AlN
, AlN
-cordierite, AlN
-堇青石， AlN
, AlN
, AlN
, AlN
rate, densification was reached at for four systems, and , whereas Dy-1210 and Er-1210 required additional holding time at to reach full density.
速率，四个系统的 致密化达到 ，而 Dy-1210 和 Er-1210 需要额外的保持时间 才能达到全密度。
Interestingly, when held at for about , the heavier rare earths, Dy-, Er-, Yb-containing systems, did reach full density, but not the lighter rare earths, , , and containing systems. When hot pressed at with a hold time of and Dy-containing systems reached full density, whereas Nd- and Sm-containing systems did not. Thus, very different hot-pressing behavior is evident for these samples. In the following, we divide these rare earths into three groups describing our observations separately.
有趣的是， 当保持大约 时，较重的稀土，含Dy，Er-，Yb的体系，确实达到了全密度，但较轻的稀土， ，， 和 含钼的体系没有。当热压时 ，含 Dy 的体系保持时间 达到全密度，而含 Nd 和 Sm 的体系则没有。因此，这些样品的热压行为明显不同。在下文中，我们将这些稀土分为三组，分别描述我们的观察结果。
(A) Lighter Rare Earths (Nd, Sm): Shrinkage curves of these samples are somewhat similar (Figs. 3(a) and (b)). The first shrinkage step occurs at for and for , followed by a second shrinkage step at . A third shrinkage step is found above . However, since this shrinkage step appears to accelerate again at higher temperatures, the third stage cannot be clearly identified and may occur at higher temperature for than for .
（A）较轻的稀土（Nd，Sm）：这些样品的收缩曲线有些相似（图3（a）和（b））。第一个收缩步骤发生在 for 和 for 处，然后是第二个 收缩步骤。第三个收缩步骤如上 图所示。然而，由于该收缩步骤似乎在较高温度下再次加速，因此无法清楚地识别第三阶段，并且可能在 比 更高的 温度下发生。
For this system in which is preferentially wetted (complete at , we identify and for eutectic melting, and and for wetting, for and systems, respectively. For melilite dissolution, is probably around For formation, is as low as according to The third shrinkage step is probably due to the dissolution of AlN in the melt, which according to the wetting experiments, should occur at . As mentioned before, these samples densify easily at but not at or . In both cases, the intermediate phase, , is retained. Some unreacted AlN also tends to remain up to .
对于优先润湿的这个系统 （完成在 ，我们分别识别 和 用于共晶熔融，以及 和 用于 润湿，用于 和 系统。对于熔体溶解， 大概在形成时， 低至 根据 第三收缩步骤可能是由于熔体中AlN的溶解，根据润湿实验，这应该发生在 。如前所述，这些样品在 或 处容易致密，但在 或 处不致密。在这两种情况下，中间阶段 都保留。一些未反应的 AlN 也倾向于保持 .
(B) Heavier Rare Earths (Er, Yb): Shrinkage curves of these samples (Figs. 4(a) and (b)) contain a shrinkage step around . The shrinkage in the -containing sample at this step is more than that in Er-1210. The next shrinkage step occurs at around and the third step occurs at around . As mentioned before, reaches full density at in the schedule of constant heating rate. However, Er1210 densifies somewhat slower and requires somewhat higher temperature. Unlike lighter rare-earth samples, both can reach full density at . The above behavior is similar to that of Y-containing materials reported by Hwang and Chen.
（B）较重的稀土（Er，Yb）：这些样品的收缩曲线（图4（a）和（b））包含收缩 步骤。在该步骤中 ，含-样品的收缩率大于Er-1210中的收缩率。下一个收缩步骤发生在 左右 ，第三步发生在 左右 。如前所述， 在恒定加热速率的时间表中 达到全密度。然而，Er1210的致密化速度稍慢，需要更高的温度。与较轻的稀土样品不同，两者都可以在 处 达到全密度。上述行为与Hwang和Chen报道的含Y材料的行为相似。
For this system in which AlN is preferentially wetted (complete at ), we identify , for eutectic formation, and , for wetting for both the and systems. Wetting of AlN is probably at a lower temperature , since the intermediate phase, , is already formed at (see Table III in part I) and AIN has disappeared. However, it does not result in a distinct shrinkage step (Figs. 4(a) and (b)). Instead, the slow shrinkage duration following is much longer in and systems compared to and systems. This is probably a manifestation of the delaying effect of AIN wetting, which tends to localize the oxide melt according to a previous study of Hwang and Chen. Lastly, -SiAION disappears before when only remains.. Thus, the third shrinkage step at around could be associated with . The formation of begins at according to part
对于AlN优先润湿的体系（完全在 ），我们确定 ，用于共晶形成，和 ，用于 和 体系的润湿。AlN的润湿可能是在较低的温度 下，因为中间相 已经形成 （见第一部分的表III），AIN已经消失。然而，它不会导致明显的收缩步骤（图4（a）和（b））。相反，与 系统 相比，慢收缩持续时间 在 and 系统中要长得多。这可能是AIN润湿延迟效应的一种表现，根据Hwang和Chen先前的研究，它倾向于定位氧化物熔体。 最后， -SiAION在 只剩下 之前消失了。 因此，大约 的第三个收缩步骤可能与 有关。的 形成从 部分 开始
(C) Intermediate Rare Earths : The two intermediate rare earth systems, Gd-1210 and Dy-1210, have more complicated shrinkage curves. They can be compared with those of lighter and heavier rare-earth systems which clarify the behavior. These are described below.
（C）中间稀土 ：Gd-1210和Dy-1210两个中间稀土体系的收缩曲线较为复杂。它们可以与更轻和更重的稀土系统进行比较，从而阐明了行为。下面将介绍这些内容。
Essentially Gd-1210 is found to behave similarly to the lighter rare earths, and systems, with a , , and shown in Fig. 5(a). As reported in part melilite formed in Gd-1210 at intermediate temperature disappeared before . This gives rise to an additional shrinkage step at around and possibly some fine feature at in the shrinkage curve shown in the Fig. 6(a). In addition, the dissolution of melilite makes it possible to densify Gd-1210 at to full density, when held for 30 min. Densification at is also achieved under constant heating rate, as in the case for Nd-1210 and Sm-1210, but without melilite remaining. Formation temperature of is again at according to part I.
从本质上讲，Gd-1210的行为与较轻的稀土 和 系统相似， 如图5（a）所示。正如部分 报道的那样，在Gd-1210中形成的melilite在中等温度下消失了 。这导致了在图6（a）所示的收缩曲线中产生 额外的收缩阶跃，并可能在收缩曲线中 产生一些精细的特征。此外，当保持30分钟时，melilite的溶解使得Gd-1210在 全密度下致密成为可能。在恒定的加热速率下也能实现致密化 ，如Nd-1210和Sm-1210的情况，但没有残留美利石。根据第一部分，地 层温度再次达到 。
Dy- 1210 is found to behave similarly to the heavier rare earths, Er-1210 and Yb-1210. In this case, and as shown in Fig. 5(b). A long delay above is also seen, presumably due to AlN trapping the liquid. Phase analysis in part I, however, found that the formed at has an unusually strong (200) reflection and that the intermediate does not exist at Also the densification rate in the last stage (above ) is very slow. These unusual features are partly due to the high viscosity of Dy containing Si-Al-O-N melt in the system. In addition we found from lattice parameters measured of annealed specimens that the lattice suddenly expands at (see Fig. 6). This strongly suggests a shift of solubility limit, expanding the single phase region, at above . It can cause further precipitation of and depletion of Dy from the melt. This reaction renders the liquid even more viscous, making Dy-1210 the hardest rare-earth SiAION to densify at .
Dy-1210 的行为与较重的稀土 Er-1210 和 Yb-1210 相似。在这种情况下， 如图5（b）所示。上面 还出现了长时间的延迟，可能是由于AlN捕获了液体。然而，第一部分的相分析发现， 形成的at 具有异常强的反射（200），并且 中间体不存在， 在最后阶段（上 图）的致密化速率非常缓慢。这些不寻常的特征部分是由于系统中含有Si-Al-O-N熔体的Dy的高粘度。 此外，我们从退火试样测量的晶格参数中发现晶格突然膨胀 （见图6）。这强烈表明溶解度极限发生了变化，扩大了单 相区域，高于 。它会导致熔体中钌的进一步沉淀 和消耗。该反应使液体更加粘稠，使 Dy-1210 成为最难致 密化的稀土 SiAION。

(3) Kinetics of Isothermal Shrinkage
（3） 等温收缩动力学

Data of isothermal shrinkage as a function of hold time are plotted in Fig. 7 for the following systems: at ,
图7绘制了以下系统的等温收缩率随保持时间的变化数据： 在 ，
Time  时间
(a)
Time (min) 时间（分钟）
(b)
(c)
Fig. 2. Shrinkage curve for (a) Li-1010, (b) , and (c) hot pressed at a constant heating rate of , showing the characteristic temperatures.
图 2.（a） Li-1010、（b） 和 （c） 热压的收缩曲线以 的恒定加热速率 ，显示了特征温度。
(a)
(b)
Fig. 3. Shrinkage curve for (a) and (b) , hot pressed at a constant heating rate of , showing the characteristic temperatures.
图 3.（a） 和（b） 的收缩曲线，热压在恒定的加热速率下 ，显示了特征温度。
Time (min) 时间（分钟）
(a)
(b)
Fig. 4. Shrinkage curve for (a) Er-1210 and (b) , hot pressed at a constant heating rate of , showing the characteristic temperatures.
图 4.（a）Er-1210和（b） 的收缩曲线，以恒定的加热速率热 压，显示了特征温度。
Time (min) 时间（分钟）
(a)
(b)
Fig. 5. Shrinkage curve for (a) Gd-1210 and (b) Dy-1210, hot pressed at a constant heating rate of , showing the characteristic temperatures.
图 5.（a） Gd-1210 和 （b） Dy-1210 的收缩曲线，以恒定的加热速率热压， 显示特征温度。
Fig. 6. Lattice parameter , for as a function of temperature.
图 6.晶格参数 ，作为 温度的函数。
Fig. 7. Isothermal shrinkage in vs for at , and at .
图 7. 等温收缩率 vs for at 和 at 。
and Nd-1210 and , both at . At these temperatures, isothermal hold brought the density to for for Nd-1210, and for . The slopes of these plots, in logarithm scale, serve as an indicator of the likely mechanism of densification. Based on Kingery's model, a dissolution/precipitation process gives rise to a slope of , whereas a higher slope is attributed to massive particle rearrangement in the presence of liquid. In all cases examined, we found the slope invariably greater than 0.5 . Thus, dissolution/precipitation cannot be the dominant process for densification in these materials until very high density.
和 Nd-1210 和 ，均位于 。在这些温度下，等温保持使 Nd-1210 和 .这些地块的斜率以对数比例表示，可作为致密化可能机制的指标。根据 Kingery 的模型， 溶解/沉淀过程导致斜率为 ，而较高的斜率归因于液体存在下的大量颗粒重排。在检查的所有情况下，我们发现斜率总是大于 0.5 。因此，在非常高的密度之前，溶解/沉淀不能成为这些材料致密化的主要过程。

IV. Discussion 四、讨论

The densification behavior of Si-Al-M-O-N systems is complicated because of the involvement of two nitride powders, the formation of intermediate phases, and the substantial variation of melt viscosity and acidity/basicity depending on the additive present. In a previous study,' the role of AlN was investigated in the Si-Al-Y-O-N system in which the oxide melt preferentially wets AIN. Our previous study further examines a number of other systems encompassing preferential wetting of either AIN or
Si-Al-M-O-N体系的致密化行为很复杂，因为两种氮化物粉末的参与，中间相的形成，以及熔体粘度和酸度/碱度的显著变化取决于存在的 添加剂。在之前的一项研究中，研究了AlN在Si-Al-Y-O-N体系中的作用，其中氧化物熔体优先润湿AIN。我们之前的研究进一步检查了许多其他系统，包括 AIN 或
Although the detailed densification behavior and reaction and reaction sequences vary, some general trends can be discerned from a comparison of characteristic temperatures. Along with our qualitative knowledge of the viscosity of these systems, a clear picture now emerges as depicted in the following.
尽管详细的致密化行为以及反应和反应序列各不相同，但从特征温度的比较中可以看出一些总体趋势。随着我们对这些系统粘度的定性了解，现在出现了一幅清晰的画面，如下图所示。

(1) Characteristic Temperatures
（1）特性温度

(A) Formation of Ternary Eutectic Oxide Melt : The first major shrinkage step is associated with this reaction. The densification mechanism in this stage is primarily redistribution of liquid, resulting in a slight improvement in the packing efficiency of the powder compact. Although the temperature of this reaction varies, it rarely provides any indication of the subsequent densification behavior. This is because of the small amount of oxide liquid formed, estimated to be around in most cases. The resultant shrinkage is relatively small, of the order of , as evident from Table II. Thus, despite a very low of in , full density is not reached until , in a constant heating rate schedule or until with an isothermal hold. In contrast, is in Nd-1210 and is for Er-1210, despite a much higher of in both.
（A） 三元共晶氧化物熔体的形成 ：第一个主要收缩步骤与该反应有关。该阶段的致密化机理主要是液体的再分布，导致粉末压块的包装效率略有提高。尽管该反应的温度各不相同，但它很少提供随后致密化行为的任何指示。这是因为形成的氧化物液体量很少，估计在大多数情况下都存在 。 由此产生的收缩相对较小，约为 ，从表二中可以明显看出。因此，尽管 in 非常低 ，但直到 在恒定的加热速率计划下或 直到等温保持时才能 达到全密度。相比之下， 在 Nd-1210 和 Er-1210 中，尽管两者的比例都高 得多。
(B) Wetting of Nitride Powders and Formation of Intermediate Phases ( and ): The second major shrinkage step is associated with the wetting of the majority nitride, . If AIN, the minority nitride, is wetted preferentially, no shrinkage step is observed at and the duration of slow shrinkage after is prolonged until as shown in Fig. 1(b). This was previously observed in and is now further verified in heavier rare-earth SiAlONs ( , and ). In these cases, liquid is thought to be trapped at AlN particles and not spread out, so that the powder compact is effectively "dry." On the other hand, if is wetted preferentially, then a gradual but substantial shrinkage step at is always seen, resulting in shrinkage of the order of or more. In addition, another shrinkage step at corresponding to AIN wetting can also be seen, also leading to substantial shrinkage over time. This is evident in systems where , and . Thus the second shrinkage step at either (if wetted first) or (if AIN wetted first), is always associated with the wetting of majority nitride powder. From Table II, it can be seen that the shrinkage at this step is of the order of or more.
（B） 氮化物粉末的润湿和中间相的形成 （ 和 ）： 第二个主要收缩步骤与大部分氮化物的润湿有关。 如果优先润湿少量氮化物AIN，则在 以下处不观察到收缩步骤，并且缓慢 收缩的持续时间延长，直到 如图1（b）所示。这在较重的稀土SiAlONs（ 和）中得到了 进一步的验证 。在这些情况下，液体被认为被困在AlN颗粒上并且不会扩散，因此粉末压块实际上是“干燥的”。另一方面，如果 优先润湿，则始终可以看到逐渐但实质性的收缩步骤 ，导致收缩量级 或更多。此外，还可以看到 与AIN润湿相对应的另一个收缩步骤，随着时间的推移也会导致大幅收缩。这在 、 和 的系统中很明显。因此 ，在（如果 先润湿）或 （如果AIN先润湿）的第二个收缩步骤总是与多数氮化物粉末的润湿有关。从表II可以看出，该步骤的收缩量级为或 更多。
(C) Dissolution Melting of Intermediate Phase : Dissolution/melting of intermediate phase, when it occurs at lower temperatures, usually results in a shrinkage step. This is seen in and for dissolution, Gd-1210 for melting, and Er-1210 and for -SiAION dissolution. (However, we did not see a distinct shrinkage step ascribed to -SiA1ON dissolution in Dy-1210, presumably because of very sluggish kinetics in this highly viscous system that limit the amount of -SiAlON formed upon ). In other systems, where is higher, hot pressing under constant heating rate can reach full density slightly below . This is the case of Nd-1210 and , for which melts at around but is and , respectively. In both cases, the dense bodies obtained still contain , as shown in Table II of part However, if the melting/dissolution temperature is too high, as in -1010 for , then full density cannot be reached even at . Thus, the final densification is often associated with dissolution/melting of intermediate phase.
（C） 中间相 的溶解熔化：中间相的溶解/熔化，当它发生在较低的温度下时，通常会导致收缩步骤。这在溶解中 可见 ，Gd-1210 用于 熔化，Er-1210 和 -SiAION 溶出。（然而，我们没有看到明显的收缩步骤归因于Dy-1210中的 -SiA1ON溶解，可能是因为这个高粘性系统中的动力学非常缓慢，限制了 - SiAlON的形成量）。在其他系统中，在较高的 条件下，热压在恒定的加热速率下可以达到略低于 的全密度。Nd-1210 和 就是这种情况，它们的 熔化程度约为 but is 和 。在这两种情况下，得到的致密体仍然含有 ，如表 II 所示 但是，如果熔化/溶解温度过高，如 -1010 中 ，则即使在 .因此，最终的致密化通常与中间相的溶解/熔融有关。
The above comparison suggests that can place an approximate lower limit for full densification temperature. Referring to Table III, we find to lie approximately between and , when the temperatures are relatively close to each other, e.g., within of each other. This is the case with , Gd, Dy, Er, and Yb. In all of the above systems, the phase assemblage at and full density still contains some intermediate phases. This implies that some dissolution and melting of intermediate phase are necessary for full densification, although full reaction is not required if isothermal hold is applied. On the other hand, when is much higher than , then either and no distinct third step is seen, as in Nd-1210 and of full densification is difficult anyway, as in Mg1010. On the other hand, when and are close to each other, then is much less than .
上述比较表明， 可以为完全致密化温度设置一个近似的下限。参考表III，我们发现 当温度彼此相对接近时，例如，彼此内部 ，大约位于 和 之间 。 Gd、Dy、Er 和 Yb 就是这种情况。在上述所有系统中，全密度的相组合 仍然包含一些中间相。这意味着中间相的一些溶解和熔融对于完全致密化是必要的，尽管如果应用等温保持，则不需要完全反应。另一方面，当 远高于 时 ，则看不到明显的第三步，如 Nd-1210 和 完全致密化是困难的，如 Mg1010。另一方面，当 和 彼此靠近时 ，则 远小于 。
It is clear that in order to achieve full densification at relatively low temperature, relatively low temperature for wetting of second nitride and dissolution/melting of the intermediate phase are required. The latter is required primarily to resupply the liquid necessary for densification. In the special case when very little intermediate phase is precipitated and hence very little liquid is expended, is irrelevant and full density can be reached essentially at . This is illustrated in the case of Dy- 1210 where is nearly lower than .
显然，为了在相对较低的温度下实现完全致密化，需要相对较低的温度来润湿第二氮化 物和中间相 的溶解/熔化。后者主要用于补充致密化所需的液体。在特殊情况下，当中间相沉淀很少，因此消耗的液体很少时， 是无关紧要的，并且基本上可以在 达到全密度。这在 Dy-1210 的情况下得到了说明，其中 几乎 低于 。
(D) Formation of : In most cases studied here, is found to be at relatively low temperature so that it is of little consequence in determining the densification temperature. The only exception is seen in Dy-1210, where formation of -SiAION apparently occurs in two stages, first at above but with low solute concentration, then above and with a much higher solute concentration. The secondary precipitation has an important effect of arresting shrinkage, so that only density is reached even at when a constant heating rate is used. As mentioned before, this observation can be understood by the effect of secondary formation on the amount of the liquid, and possibly its viscosity as well. This material must be densified by holding at below '.
（D）的 形成：在这里研究的大多数情况下，发现处于相对较低的温度下， 因此对确定致密化温度影响不大。唯一的例外是在Dy-1210中，其中-SiAION的 形成显然分两个阶段发生，首先在上方 但溶质浓度较低，然后在上方 且溶质浓度高得多。二次 降水具有阻止收缩的重要作用，因此即使在使用恒定加热速率 的情况下也只能 达到密度。如前所述，这一观察结果可以通过二次 形成对液体量的影响来理解，也可能对液体的粘度产生影响。这种材料必须通过保持在以下 来致密。
The characteristic temperatures, except , are expected to vary with the composition. In fact, is expected to be independent of composition in systems with one eutectic in the system at low nitrogen content. In systems like or with more than one eutectic in the system, will depend on the initial oxide composition. The values of and are dictated by the basicity of the melt which controls the wetting behavior and hence the formation of the intermediate phases. For example, moving toward the corner on the -SiAlON will decrease the basicity of the melt, resulting in an increase in the value of and a decrease in the value of . The value of will depend on the intermediate phase formed. For example, decreasing the amount of is expected to result in formation of intermediate phases with a higher ratio, which will change the value of . The value of is also expected to change with composition. Higher basicity is expected to result in a decrease in the value of .
除 外 ，特征温度预计会随成分而变化。事实上， 在低氮含量 的系统中，预计与系统中具有一个共晶 的组成无关。在类似 或 系统中具有多个共晶的 系统中， 将取决于初始氧化物组成。 和 的值由熔体的碱度决定，熔体的碱度控制着润湿行为，从而控制着中间相的形成。 例如， 向 -SiAlON 的 拐角移动会降低熔体的碱度，从而导致 的 值增加和值的减小。的 值将取决于形成的中间相。例如，减少 的量预计会导致形成具有更高 比率的中间相，这将改变 的值。的 值预计也会随着成分的变化而变化。碱度越高，预计 .

(2) Amount and Viscosity of Liquid
（2）液体的量和粘度

Liquid phase is obviously of central importance for densification of M-SiALON. The amount of the liquid in the first stage upon eutectic melt formation is determined by the phase diagram. The amount of liquid in the tertiary stage is
液相显然对M-SiALON的致密化至关重要。共晶熔体形成后第一阶段的液体量由相图确定。 第三阶段的液体量为
affected by the dissolution/melting of the intermediate phase, and in special cases even by the secondary precipitation of . In addition, the distribution of liquid is also relevant, as in the case of the preferential wetting of AIN. In all circumstances, when the amount of liquid is severely reduced because of precipitation or localization, densification is retarded.
受中间相溶解/熔融的影响，在特殊情况下甚至受二 次沉淀的影响。此外，液体的分布也很重要，例如AIN的优先润湿情况。在所有情况下，当液体量因沉淀或局部化而严重减少时，致密化就会延迟。
Viscosity of the liquid is also expected to have an effect on the densification kinetics. This effect, however, is obscured in most cases by the different characteristic temperatures that vary widely among various systems. For example, although the density achieved under constant heating rate decreases in the order of , and , reflecting the increasing viscosity in the same order, at above this trend is countered by the decreasing melting temperature of in the same order, resulting in very rapid densification of Gd-1210. (The faster kinetics of Gd- 1210 at are also confirmed by the lattice parameter data of -SiAION in Table I of part I, where the cell size of -SiAION at is seen to be much larger than that of Nd-1210 and Sm-1210, even though the Gd ion is smaller.)
预计液体的粘度也会对致密化动力学产生影响。然而，在大多数情况下，这种影响被不同系统之间差异很大的不同特征温度所掩盖。例如，尽管在恒定加热速率下达到的密度以 和 的顺序降低，反映了粘度以相同的顺序增加， 但在高于 此趋势时，熔化温度的降低会抵消相同顺序的 熔化，导致 Gd-1210 的致密化非常快。 （Gd-1210 at 的更快动力学也由第一部分表 I 中 -SiAION 的 晶格参数数据证实， 其中 -SiAION at 的细胞大小比 Nd-1210 和 Sm-1210 的细胞大小大得多，即使 Gd 离子更小。
Likewise, in heavier rare-earth SiAlONs, although we found in isothermal hot pressing that the densification time at increases slightly in the order of Dy, Er, and Yb, probably due to the influence of viscosity, the densification kinetics in constant heating rate do not reflect the same trend, because of nonmonotonic variation of characteristic temperatures.
同样，在较重的稀土SiAlONs中，尽管我们发现在等温热压中，致 密化时间在Dy、Er和Yb的顺序上略有增加，可能是由于粘度的影响，但由于特征温度的非单调变化，恒定加热速率下的致密化动力学并不反映相同的趋势。

V. Conclusions 五、结论

(1) Reaction densification of M-SiAlON occurs in three stages. The first stage is associated with the formation of the ternary eutectic (at temperature ). The second stage is associated with the preferential wetting of majority nitride powder . This occurs at when is wetted first. If AIN is wetted first, then no shrinkage step is observed at and the densification is delayed until , when is wetted finally.
（1）M-SiAlON的反应致密化分三个阶段进行。第一阶段与 三元共晶的形成有关（在温度 下）。第二阶段与多数氮化物粉末的优先润湿有关 。这发生在第一次润湿 时 。如果先润湿 AIN，则在 处没有观察到收缩步骤，致密化延迟到 最终润湿时。
(2) The third stage involves the dissolution/melting of the intermediate phase (at temperature ) if is low; otherwise a distinct third stage is not seen while a gradual densification continues following the second stage. In the extreme case of very high , this may result in poor density as in the case of Mg-1010.
（2）第三阶段涉及中间相（在温度 下）的溶解/熔化，如果 温度较低;否则，看不到明显的第三阶段，而在第二阶段之后继续逐渐致密化。在极端情况下 非常高 ，这可能会导致密度低，如Mg-1010的情况。
(3) The formation temperature of the final phase is not crucial in most cases, unless a sudden secondary precipitation of -SiAlON at the later stage drains the liquid and retards densification. Such material must be densified at temperatures below .
（3）在大多数情况下，最后 阶段的形成温度 并不重要，除非后期 -SiAlON的突然二次沉淀排 出液体并延缓致密化。这种材料必须在低于 的温度下致密化。
(4) To achieve full densification at relatively low temperature, a low wetting temperature for the second nitride and low dissolution/melting temperature of the intermediate phase are required.
（4）为了在相对较低的温度下实现完全致密化，需要第二氮化 物的低润湿温度和中间相 的低溶解/熔融温度。
(5) The dominant process for densification in these materials is massive particle rearrangement, although some dissolution facilitates full densification by providing the necessary liquid. More generally, the amount of liquid is controlled by the phase diagram, dissolution/melting of intermediate phase, distribution of liquid, and secondary precipitation of SiAlON.
（5）这些材料中致密化的主要过程是大量颗粒重排，尽管一些溶解通过提供必要的液体促进了完全致密化。更一般地说，液体的量由相图、中间相的溶解/熔化、液体的分布和SiAlON的 二次沉淀控制。
(6) The effect of viscosity of liquid is relatively insignificant compared to that of the amount of liquid for reaction densification of -SiAlON.
（6）与 -SiAlON反应致密化的液体量相比，液体粘度的影响相对不显著。

References 引用

P. Drew and M. H. Lewis, "The Microstructure of Silicon Nitride Ceramics during Hot-Pressing Transformations," J. Mater. Sci., 9, 261-69 (1974).
P. Drew 和 M. H. Lewis，“热压转型过程中氮化硅陶瓷的微观结构”，J. Mater。科学， 9， 261-69 （1974）.
M. H. Lewis, B. D. Powell, P. Drew, R. J. Lumby, B. North, and A. J. Taylor, "The Formation of Single-Phase Si-Al-O-N Ceramics," J. Mater. Sci., 12, 6174 (1977).
M. H. Lewis、BD Powell、P. Drew、RJ Lumby、B. North 和 AJ Taylor，“单相 Si-Al-O-N 陶瓷的形成”，J. Mater。科学， 12， 6174 （1977）.
M. H. Lewis, A. R. Bhatti, R. J. Lumby, and B. North, "The Microstructure of Sintered Si-Al-O-N Ceramics," J. Mater. Sci., 15, 103-13 (1980).
M. H. Lewis、A. R. Bhatti、RJ Lumby 和 B. North，“烧结 Si-Al-O-N 陶瓷的微观结构”，J. Mater。科学， 15， 103-13 （1980）.
M. H. Lewis and R. J. Lumby, "Nitrogen Ceramics: Liquid Phase Sintering," Powder Metall., 26 [2] 73-81 (1983).
M. H. Lewis 和 RJ Lumby，“氮陶瓷：液相烧结”，Powder Metall.，26 [2] 73-81 （1983）。
G. K. Layden, "Process Development for Pressureless Sintering of SiAION Ceramic Components," Report No. R175-91072-4. United Technologies Research Center, Feb. 1976.
G. K. Layden，“SiAION陶瓷部件无压烧结工艺开发”，报告编号R175-91072-4。联合技术研究中心，1976年2月。
S. Boskovic, L. J. Gauckler, G. Petzow, and T. Y. Tien, "Reaction Sintering Forming Solid Solution in the System Si,Al/N,O I: Sintering of AlN Mixtures," Powder Metall. Int., 9 [4] 185-89 (1977).
S. Boskovic、L. J. Gauckler、G. Petzow 和 T. Y. Tien，“系统 Si，Al/N，O I 中的反应烧结形成 固溶体：AlN 混合物的 烧结”，Powder Metall。 国际， 9 [4] 185-89 （1977）.
S. Boskovic, L. J. Gauckler, G. Petzow, and T. Y. Tien, "Reaction Sintering Forming Solid Solution in the System Si,Al/N,O II: Sintering of -AIN Mixtures," Powder Metall. Int., 10 [4] 180-85 (1978).
S. Boskovic、L. J. Gauckler、G. Petzow 和 T. Y. Tien，“Si，Al/N，O II 系统中的反应烧结形成 固溶体：-AIN 混合物的 烧结”，Powder Metall。 国际， 10 [4] 180-85 （1978）.
S. Boskovic, L. J. Gauckler, G. Petzow, and T. Y. Tien, "Reaction Sintering Forming Solid Solution in the System Si,Al/N,O III: Sintering of AlN- Mixtures," Powder: Metall. Int., 11 [4] 169-71 (1979).
S. Boskovic、L. J. Gauckler、G. Petzow 和 T. Y. Tien，“系统 Si，Al/N，O III 中的反应烧结形成 固溶体：AlN- 混合物的 烧结”，粉末：金属。 国际， 11 [4] 169-71 （1979）.
M. N. Rahman, F. L. Riley, and R. J. Brook, "Mechanisms of Densification during Reaction Hot-Pressing in the System Si-Al-O-N," J. Am. Ceram. Soc., 63 [11-12] 648-53 (1980).
M. N. Rahman、F. L. Riley 和 RJ Brook，“Si-Al-O-N 系统中反应热压过程中致密化的机制”，J. Am. Ceram。Soc.， 63 [11-12] 648-53 （1980）.
M. Kubawara, M. Benn, and F. L. Riley, "The Reaction Hot Pressing of Compositions in the System Al-Si-O-N Corresponding to -SiAlON," J. Mater. Sci., 15, 1407-16 (1980)
M. Kubawara、M. Benn 和 F. L. Riley，“对应于 -SiAlON 的系统中组合物的反应热压”，J. Mater。科学， 15， 1407-16 （1980）
M. Havier and P. L. Hansen, "Hot-Pressing and " Phase Transformation of Compositions Corresponding to -SiAlON," J. Mater. Sci., 25, 992-96 (1990).
M. Havier 和 P. L. Hansen，“热压和 ”对应于 -SiAlON 的组合物的相变“，J. Mater。科学， 25， 992-96 （1990）.
S. L. Hwang and I-Wei Chen, "Reaction Hot Pressing of '- and '- SiAlON Ceramics," J. Am. Ceram. Soc., 77 [1] 165-71 (1994).
S. L. Hwang 和 I-Wei Chen，“SiAlON 陶瓷的反应热压 ”，J. Am. Ceram。Soc.， 77 [1] 165-71 （1994）.
. Menon, and I-Wei Chen, "Reaction Densification of '-SiAlON: I Wetting Behavior and Acid-Base Reactions," J. Am. Ceram. Soc., 78 [3] 54552 (1995).
。Menon 和 I-Wei Chen，“ '-SiAlON 的反应致密化：I 润湿行为和酸碱反应”，J. Am. Ceram。Soc.， 78 [3] 54552 （1995）.
J. E. Shelby and J. T. Kohli, "Rare-Earth Aluminosilicate Glasses," J. Am. Ceram. Soc., 73 [1] 39-42 (1990).
J. E. Shelby 和 J. T. Kohli，“稀土铝硅酸盐玻璃”，J. Am. Ceram。Soc.， 73 [1] 39-42 （1990）.
K. P. J. O'Reilly, M. Redington, S. Hampshire, and M. Liegh, "Parameters Affecting Pressureless Sintering of -SiAlONs with Lanthanide Modifying Cations"; pp. 393-98 in Silicon Nitride Ceramics Scientific and Technological Advances, Proceedings of Materials Research Society Symposium, 287 (Boston, MA, Nov. 30-Dec. 3, 1992). Edited by I-Wei Chen, P. F. Becher, M. Mitomo, G. Petzow, and T. S. Yen. Materials Research Society, Pittsburgh, PA, 1993.
K. P. J. O'Reilly、M. Redington、S. Hampshire 和 M. Liegh，“影响镧系改性阳离子 -SiAlON 无压烧结的参数”;第 393-98 页，氮化硅陶瓷科学技术进展，材料研究学会研讨会论文集，287（马萨诸塞州波士顿，1992 年 11 月 30 日至 12 月 3 日）。由 I-Wei Chen、P. F. Becher、M. Mitomo、G. Petzow 和 T. S. Yen 编辑。材料研究学会，宾夕法尼亚州匹兹堡，1993 年。
W. D. Kingery, J. M. Woulbroun, and F. R. Charvat, "Effects of Applied Pressure on Densification during Sintering in Presence of a Liquid Phase," J. Am. Ceram. Soc., 46 [8] 391-95 (1963).
W. D. Kingery、J. M. Woulbroun 和 F. R. Charvat，“液相存在下烧结过程中施加压力对致密化的影响”，J. Am. Ceram。Soc.， 46 [8] 391-95 （1963）.
E. M. Lewis, C. R. Robbins, and H. F. McMurdie, Figs. 459 for Li, 630 for Ca, 712 for Mg, and 2586 for in Phase Diagrams for Ceramists. Edited by M. K. Reser. American Ceramic Society, Columbus, OH, 1969.
E. M. Lewis、C. R. Robbins 和 H. F. McMurdie，图 459 表示 Li，图 630 表示 Ca，712 表示 Mg，图 2586 表示陶器家 的相图。由 MK Reser 编辑。美国陶瓷协会，俄亥俄州哥伦布市，1969 年。
. M. Erbe, and D. E. Day, "Properties of Glasses for in Vivo Applications," J. Am. Ceram. Soc., 73 [9] 2708-13 (1990).
。M. Erbe 和 D. E. Day，“体内应用眼镜的特性 ”，J. Am. Ceram。Soc.， 73 [9] 2708-13 （1990）.
Y. Murakami and H. Yamamoto, "Phase Equilibria and Properties of Glasses in the System," J. Ceram. Soc. Jpn, 101 [10] 1101-106 (1993)
Y. Murakami 和 H. Yamamoto，“ 系统中玻璃的相平衡和性质”，J. Ceram。Soc. Jpn， 101 [10] 1101-106 （1993）
Y. B. Cheng and D. P. Thompson, "Aluminum-Containing Nitrogen Melilite Phases," J. Am. Ceram. Soc., 77 [1] 143-48 (1994).
Y. B. Cheng 和 D. P. Thompson，“含铝氮熔岩相”，J. Am. Ceram。Soc.， 77 [1] 143-48 （1994）.
  1. S. C. Danforth—contributing editor
    S. C. Danforth—特约编辑