Particle erosion of C/C-SiC composites with different Al

J Cent South Univ (2020) 27 2557minus2566 DOI httpsdoiorg101007s11771-020-4481-0

Particle erosion of CC-SiC composites with different Al addition in reactive melt infiltrated Si

LIU Lei(刘磊)1 FENG Wei(冯薇)1 LI Bo-yan(李博岩)1 LI Jian-ping(李建平)1 ZHANG Lei-lei(张磊磊)2 GUO Yong-chun(郭永春)1 HE Zi-bo(何子博)1 CAO Yi(曹毅)2 BAO Ai-lin(包艾琳)1

1 School of Materials and Chemical Engineering Xirsquoan Technological University Xirsquoan 710021 China

2 State Key Laboratory of Solidification Processing Northwestern Polytechnical University Xirsquoan 710072 China

copy Central South University Press and Springer-Verlag GmbH Germany part of Springer Nature 2020

Abstract Particle erosion of CC-SiC composites prepared by reactive melt infiltration with different Al addition was studied by gas-entrained solid particle impingement test SEM EDS and XRD were performed to analyze the composites before and after erosion The results indicate that a U shape relationship curve presents between the erosion rates and Al content and the lowest erosion rate occurs at 40 wt Al Except for the important influence of compactness the increasing soft Al mixed with reactive SiC namely the mixture located between carbon and residual Si also plays a key role in the erosion of the CC-SiC composites through crack deflection plastic deformation and bonding cracked Si Key words CC-SiC Al addition reactive melt infiltration solid particle erosion Cite this article as LIU Lei FENG Wei LI Bo-yan LI Jian-ping ZHANG Lei-lei GUO Yong-chun HE Zi-bo CAO Yi BAO Ai-lin Particle erosion of CC-SiC composites with different Al addition in reactive melt infiltrated Si [J] Journal of Central South University 2020 27(9) 2557minus2566 DOI httpsdoiorg101007s11771-020-4481-0

1 Introduction

CC-SiC composites have great potential in many fields due to their low density high strength good wear resistance and outstanding thermal stability [1minus5] They can be used as housings and structural elements for optical systems [6] throat insert or nozzle [7] turbine engine blade [8] piston of internal combustion engine [9] brake disc of high speed or heavy vehicles [10] armor [11] and so on In service they will be damaged by space debris un-burnt particles fine sand fragments and other solid particles In other word the strength and

lifespan of corresponding structural component would be weakened drastically by the particle flow For example the life of helicopter rotor blade decreased to 18 designed by solid particle erosion [12] and ablation rate of the composites in particle erosion environment was much higher than that without particle erosion [13 14]

Up to now particle erosion of polymer matrix composites [15] metal [16] and ceramic [17] has been greatly studied However to our best knowledge few papers can be found on the erosion of the CC-SiC composites induced by particle flow It has been found that both more SiC and fewer pores are beneficial for the anti-erosion of CC

Foundation item Project(51902239) supported by the National Natural Science Foundation of China Project(2020JQ-808) supported by

the Science and Technology Fund of Shaanxi Province China Projects(19JK0400 19JK0402) supported by the Education Fund of Shaanxi Province China Project(SKLSP201752) supported by the State Key Laboratory of Solidification Processing in Northwestern Poly Technical University China Project(XAGDXJJ17008) supported by the Principal Fund of Xirsquoan Technological University China Project supported by the Youth Innovation Team of Shaanxi Universities China

Received date 2020-01-18 Accepted date 2020-06-19 Corresponding author LIU Lei PhD Lecturer Tel +86-29-83208080 E-mail liuleiNIN126com ORCID httpsorcidorg0000-

0003-3168-7303 FENG Wei PhD Lecturer Tel +86-29-83208080 E-mail cindybear126com ORCID httpsorcidorg0000-0003-4013-0603

J Cent South Univ (2020) 27 2557minus2566

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composites [18minus21] And the interface composition is important to the erosion resistance of SiCfSiC composites [22] To make CC-SiC composites more competent for application there has been strong interest in optimizing their ingredients and microstructures to develop the erosion resistance [23] Ductile Al modified CC-SiC composites have lower preparation temperature [24] reduced manufacturing time and cost [25] higher bending strength and fracture toughness [26] and better oxidation [27] and ablation resistance [28] Besides based on our previous work that adding different Al in infiltrated Si could change the mechanical properties of CC-SiC composites [24] and referencing the outstanding erosion resistance of ER7 and black gold coatings [12] which came from the optimization of soft and hard element it can be inferred that certain amount of Al addition might improve anti-erosion ability of CC-SiC composites To understand how Al addition works on the erosion CC-SiC composites were prepared by reactive melt infiltration and evaluated by gas- entrained solid particle impingement test Evolutions of microstructure morphology and elementphase distribution before and after erosion were mainly investigated to reveal the mechanism 2 Experimental procedure 21 Composites preparation Porous skeletons with size of 12 mmtimes12 mmtimes 12 mm were cut from a bulk CC composite which was thermal gradient chemical vapor infiltrated 25D needle punched fabric Densities of the fabric before and after infiltration of pyrocarbon were 045 and 095 gcm3 respectively The cut skeletons were cleaned in distilled water for 05 h by ultrasonic wave and then dried at 100 degC for 24 h Meanwhile mixed powders of Si and Al with different ratios were prepared by ball milling for 1minus2 h The Si powder was 45minus55 μm and the Al powder was 80minus120 μm Then the CC skeletons were embedded into the powder mixtures in a graphite crucible and heat treated at 1100minus1200 degC for 1minus3 h in 10minus2 Pa vacuum After furnace cooling the Si-Al infiltrated CC composites were taken out from the crucible and hand-abraded with 80 and 400 grit SiC papers to remove the surface adhered powders and reacted phases Finally samples with dimensions of 11 mmtimes11 mmtimes11 mm were hand-

polished by 400 grit SiC papers for test 22 Tests and characterization The density of the prepared composite was determined by drainage according to Archimedean principle The erosion test was performed at room temperature in a gas-blast device which was manufactured according to ASTM G76-2007 The main parameters are listed in Table 1 and the test is illustrated in Figure 1 Compressed air-entrained 50minus115 μm angular Al2O3+5 wt iron-oxide particles were accelerated in an alundum nozzle tube and then sprayed from the end of the nozzle and impinged vertically to the sample surface for 20 s from 10 mm distance The impinging stream was parallel to the web and non woven layer as shown in Figure 1 Inner diameter and length of the nozzle tube were 3 and 100 mm respectively Pressure of the air was 04 MPa and the particle feed rate was 600 mgs The particle impact velocity was 70 ms which was measured by the rotating double-disk method The linear and mass erosion rates were calculated according to Eqs (1) and (2)

l =d

Rt

(1)

m =m

Rt

(2)

where Rl is linear erosion rates Δd is the change of the samplersquos thickness at centre region before and after erosion Rm is the mass erosion rate Δm is the change of the mass before and after erosion t is erosion time The samples were measured and weighed at the accuracies of 1 μm and 01 mg respectively The phase analyses of the prepared composite were conducted by X-ray diffraction (XRD XrsquoPert Pro MPD) Morphology and chemical composition were investigated by scanning electron microscopy (SEM JSM6460) combined with energy dispersive spectroscopy (EDS) Table 1 Key parameters of erosion test

Parameter Value

Carrier air pressureMPa 04

Nozzle lengthmm 100

Inner diameter of nozzlemm 3

Al2O3 particle flux(mgsminus1) 600

Distance from nozzle end to samplemm 10

Impact angle(deg) 90

Impact velocity(msminus1) 70

Test durations 20


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Figure 1 Schematic of erosion test method (a) and morphology and XRD pattern of impacted solid particles (b)

3 Results and discussion 31 Microstructure of CC-SiC composites Representative cross-section morphologies of the prepared CC-SiC composites with different Al content are shown in Figure 2 To make the following discussion convenient the CC-SiC composites prepared with Si powder containing 0 10 20 30 40 and 50 (wt) Al were labeled as CC-SiC-0Al CC-SiC-10Al CC-SiC- 20Al CC-SiC-30Al CC-SiC-40Al and CC-SiC- 50Al respectively The densities of CC-SiC-0Al and CC-SiC-10Al were similar (095 gcm3) while these of CC-SiC-20Al CC-SiC-30Al and CC- SiC-40Al were about 200 gcm3 When the Al content increased to 50 wt the density of composites was 115 gcm3 Obviously CC-SiC- 20Al CC-SiC-30Al and CC-SiC-40Al got better infiltration than others which was in accordance with the morphology in Figure 2 Some white phases located at the porous black skeleton of CC-SiC-0Al and CC-SiC-50Al while CC-SiC- 20Al and CC-SiC-40Al were compact and composed of white grey and black phases Moreover the content of grey phase in CC-SiC- 40Al was more than that in CC-SiC-20Al EDS analysis indicated that the white phase was Si and the black phase was carbon Besides structures of all the composites were overlapped layers of non-woven layer X web and non-woven layer Y which were determined by the needle punched fibers fabric To better understand the microstructure of the prepared composites highly magnified webs of

CC-SiC-0Al CC-SiC-20Al CC-SiC-40Al and CC-SiC-50Al are shown in Figure 3 It was clear that there were some pores and holes in CC-SiC-0Al and CC-SiC-50Al whereas the interspaces in CC skeletons of CC-SiC-20Al and CC-SiC-40Al were filled completely by grey and white phases Moreover some white particles located at the cavity of CC-SiC-0Al while thin integrated white shell coated on the pyrocarbon which enwrapped carbon fiber in CC-SiC-50Al EDS analysis indicated that the white particle in CC-SiC-0Al was a compound of C and Si and the shell around carbon in CC-SiC-50Al was composed of C Si and Al In CC-SiC-20Al and CC-SiC-40Al the white phase was Si and the grey phase was a mixture of C Si and Al The grey phase layer between black carbon and white Si in CC-SiC-40Al was thicker than that in CC-SiC- 20Al and contained more Al Besides a few cracks could be found in CC-SiC-20Al and they located at interface of carbon and grey layer (marked as Crack I) Nevertheless a number of cracks distributed in CC-SiC-40Al Not only more Cracks I but also a great deal of micro-cracks in the thicker grey layer (marked as Crack II) were found in CC-SiC-40Al Figure 4 shows the XRD patterns of the prepared composites The results indicate that CC-SiC-0Al consists of carbon and SiC and CC-SiC-20Al and CC-SiC-40Al are composed of carbon SiC Al and Si while CC-SiC-50Al is composed of carbon SiC and Al4C3 It is obvious that CC-SiC-40Al has more Al than others according to the relative intensities of Al diffraction peaks at 3847deg 4474deg 6513deg and 7823deg In another words the Al content of composites


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Figure 2 Backscattered electron morphology of prepared CC-SiC composites (a) CC-SiC-0Al (b) CC-SiC-20Al

(c) CC-SiC-40Al (d) CC-SiC-50Al

increased with the rising ratio of Al in infiltrated Si and up to the maximum at 40 wt And then Al4C3 appeared at 50 wt Al This implies that the Al in Si powder should not exceed 40 wt since the Al4C3 is an unstable phase which is always avoided during composites fabrication Moreover no oxides are found in the XRD analysis which seems to be inconsistent with the EDS analysis in Figure 3 This should result from the low content of oxygen which might solute in Al Besides in combination with analysis of Figure 3 the grey layers in CC-SiC- 20Al and CC-SiC-40Al should be a mixture of SiC and Al 32 Erosion property of CC-SiC composites The erosion rates of the prepared composites are shown in Figure 5 The linear and mass erosion rates presented good consistency and the relationship between the erosion rates and Al content was a U shape curve The sudden decline and rise of erosion rates happened at 10minus20 and 40minus50 Al (mass fraction) which were adversely proportional to the densities of composites Besides CC-SiC-20Al CC-SiC-30Al and CC-SiC-40Al had similar densities but different erosion rates The better erosion resistance of CC-SiC-40Al should

come from their diverse microstructures and phase compositions Figure 6 shows the eroded morphology of the CC-SiC composites corresponding to Figure 2 The web layer at surface of CC-SiC-0Al was depleted by solid particles Differently non-woven layers of CC-SiC-20Al and CC-SiC-40Al were destructed more seriously than the web while the different layers in CC-SiC-50Al possessed near anti-erosion ability Obviously the web layer was strengthened by infiltrated Si Al and the product of SiC Moreover the survived web layers of CC-SiC-20Al and CC-SiC-40Al were also different although they had similar high densities The residual phases of web layer at the surface of CC-SiC-40Al were segregated by each other but flat on the whole Nevertheless block white phases in the eroded web of CC-SiC-20Al were separated Thus it can be inferred that the erosion mechanism varied with the density and Al content of the prepared CC-SiC composites The highly magnified webs of the eroded CC-SiC composites are shown in Figure 7 Compared with Figure 3(a) cracked carbon matrix and broken fiber in Figure 7(a) indicate that both carbon fiber and matrix are brittle The debonding


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Figure 3 Backscattered electron morphology of prepared CC-SiC composites at high magnification and relative EDS

analysis (a) CC-SiC-0Al (b) CC-SiC-20Al (c) CC-SiC-40Al (d) CC-SiC-50Al (e) EDS analysis of Spot 1

(f) EDS analysis of Spot 2

Figure 4 XRD patterns of prepared CC-SiC composites

Figure 5 Erosion rates of CC-SiC composites as

function of Al content


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of fiber and matrix implies that more energy was consumed during the damage of the CC skeleton To the compact CC-SiC-20Al and CC-SiC-40Al the eroded morphologies are also distinct At surface of CC-SiC-20Al eroded carbon fiber carbon matrix and other matrix phases kept good adherence to each other and there were no cracks among them Only some cracked Si (indicated by arrow) distributed on the Si block However the Si (indicated by arrow) in CC-SiC-40Al cracked completely but most of them adhered to the surface Moreover the fiber and matrix debonded (indicated by circle) and some fiber were peeled off (marked by ellipse) Thus it could be concluded that the more Al and micro-cracks not only changed the failure mode of matrix but also affected the breakage of pyrocarbon surrounded fiber At the damaged surface of CC-SiC-50Al there were broken matrix debonded fiber and matrix sheaths which came from removed fibers The eroded characteristics of CC-SiC-50Al were similar to CC-SiC-40Al except for the adhered Si particles which should be caused by the different densities To further clarify the erosion mechanism of the compact CC-SiC composites the eroded morphologies of non-woven layer and representative matrix in web of CC-SiC-20Al and

CC-SiC-40Al are shown in Figure 8 Obviously non-woven layer of CC-SiC-20Al was flat and few pull-out fibers can be found which indicates that the fracture of fiber and matrix were synchronous However the non-woven layer of CC-SiC-40Al was ladder-shaped which resulted from the detached and removed fibers (indicated by arrow) This was in accordance with the eroded characteristic in Figures 7(b) and (c) From Figures 8(c) and (d) it could be found that some scuffs (indicated by arrow) were at surface of both composites and the scuffs in CC-SiC-40Al were shallower and shorter Thus it can be inferred that the damage of CC-SiC-20Al induced by impacted particles was more serious Moreover some craters and platelets (indicated by ellipse) induced by scraping and extrusion located at the surface of CC-SiC-40Al which was the representative feature of ductile materials 33 Erosion mechanism of CC-SiC composite To the CC-SiC composites in this study there were several key constituents including carbon fiber carbon matrix Si matrix a mixture matrix of SiC and Al some pores and micro-cracks The all constituents were smaller than the impacted Al2O3 particles During normal impact of particles brittle

Figure 6 Eroded morphology of prepared CC-SiC composites (a) CC-SiC-0Al (b) CC-SiC-20Al (c) CC-SiC-40Al

(d) CC-SiC-50Al


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Figure 7 Morphology of eroded web of CC-SiC composites (a) CC-SiC-0Al (b) CC-SiC-20Al (c) CC-SiC-40Al

(d) CC-SiC-50Al (Figures at corner of (b) and (c) show relative backscattered electron morphology)

materials tend to crack while erosion of ductile materials involves scraping and extrusion of material to form ridges that are vulnerable to be attacked by other particles [29] Thus the erosion of the CC-SiC composites should involve gouging by sharp corner and strike by blunt edge of the impacted particles Meanwhile the impact of particles would induce crack of carbon fiber pyrocarbon matrix and Si matrix plastic deformation of the SiC and Al mixture and debonding of different constituents The schematic diagram of particle erosion of prepared CC-SiC composites with different Al content in infiltrated Si is shown in Figure 9 For CC-SiC-0Al as shown in Figure 9(a) crack expansion followed fracture of pyrocarbon matrix then fiber broken and finally damage of CC skeleton happened which was similar to the erosion of CC composites [20] The high porosity in web reduced the bearing components and accelerated the crack propagation which resulted in the severe erosion To the compact CC-SiC-20Al and CC-SiC- 40Al the infiltrated Si Al and formed SiC improved the erosion resistance greatly Their

different erosion rates mainly came from the influence of Al contents in infiltrated Si High Al content in the composites not only resulted in thicker SiC+Al layer but also induced more micro-cracks (Figure 3) The SiC+Al layer could deform under impact of particle while micro-cracks would prolong the expending path of crack (Figures 9(b) and (c)) In other words more Al in the matrix could absorb more impact energy through plastic deformation and crack deflection which could weaken the fragmentation of nearby brittle Si And the Al also bonded the cracked Si and protected them from removal (Figure 7(c)) The residual cracked Si in turn prevented the binder Al from plowing cutting and gouging Thus both CC-SiC-20Al and CC-SiC-40Al were well infiltrated but CC-SiC-40Al presented better particle erosion resistance When the Al content in infiltrated Si increased to 50 wt the excessive reaction between Al and carbon inhibited the infiltration of molten Al-Si which led to the low density of CC-SiC-50Al Although the SiC and Al4C3 around pyrocarbon matrix modified the anti-erosion ability of web (Figure 9(d)) the massive pores resulted in the high


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Figure 8 Eroded morphology of CC-SiC composites (a) Non-woven layer of CC-SiC-20Al (b) Non-woven layer of

CC-SiC-40Al (c) Matrix in web of CC-SiC-20Al (d) Matrix in web of CC-SiC-40Al (Inserted figures at corner are

relative backscattered electron morphology)

Figure 9 Schematic diagram of particle erosion of prepared CC-SiC composites with different Al content in infiltrated

Si (a) CC-SiC-0Al (b) CC-SiC-20Al (c) CC-SiC-40Al (d) CC-SiC-50Al


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erosion rates In summary the increasing Al in infiltrated Si powder caused different densities and microstructures of prepared CC-SiC composites The density was a key factor for erosion resistance Besides to the compact CC-SiC the Al content and micro-cracks in composites were important to the consumption of impact energy of particles 4 Conclusions CC-SiC composites are prepared by reactive melt infiltration with different Al additions Gas-entrained solid particle impingement test reveals a U shape relationship curve between the erosion rates and Al content with the lowest linear and mass erosion rates occurring at 40 wt Al Eroded morphology suggests that a high compactness of the composites could improve the erosion resistance effectively and the increasing soft Al could further strengthen the anti-erosion ability Besides fracture crack deflection Al plastic deformation and peeling off of cracked Si from Al substrate also play key roles in the consumption of impact energy during erosion Contributors LIU Lei provided the concept composite preparing technique and test method and wrote the original draft FENG Wei conducted the literature review data curation and original draft review LI Bo-yan and ZHANG lei-lei prepared the composite and performed the erosion test LI Jian-ping and GUO Yong-chun analyzed the erosion data HE Zi-bo CAO Yi and BAO Ai-lin edited the draft of manuscript All authors replied to reviewers comments and revised the final version Conflict of interest LIU Lei FENG Wei LI Bo-yan LI Jian-ping ZHANG Lei-lei GUO Yong-chun HE Zi-bo CAO Yi and BAO Ai-lin declare that they have no conflict of interest

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中文导读

Al 添加量对反应熔渗 CC-SiC 复合材料粒子冲蚀特性的影响摘要本文基于气固两相流冲击测试方法对反应熔渗中添加不同 Al 含量的 CC-SiC 粒子的冲蚀特

性进行了研究采用 SEMEDS 以及 XRD 对材料冲蚀前后的形态微结构物相等进行了分析结

果表明冲蚀率和 Al 添加量之间呈 U 型曲线关系除材料致密度对其抗冲蚀性有重要影响外分布

在碳和残余 Si 之间的混合物即 SiC 混杂塑性 Al通过塑性变形诱导裂纹偏转粘连碎裂 Si 等耗

能方式也对材料的冲蚀行为和耐冲蚀能力起重要作用关键词CC-SiC添加 Al反应熔渗固态粒子冲蚀


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composites [18minus21] And the interface composition is important to the erosion resistance of SiCfSiC composites [22] To make CC-SiC composites more competent for application there has been strong interest in optimizing their ingredients and microstructures to develop the erosion resistance [23] Ductile Al modified CC-SiC composites have lower preparation temperature [24] reduced manufacturing time and cost [25] higher bending strength and fracture toughness [26] and better oxidation [27] and ablation resistance [28] Besides based on our previous work that adding different Al in infiltrated Si could change the mechanical properties of CC-SiC composites [24] and referencing the outstanding erosion resistance of ER7 and black gold coatings [12] which came from the optimization of soft and hard element it can be inferred that certain amount of Al addition might improve anti-erosion ability of CC-SiC composites To understand how Al addition works on the erosion CC-SiC composites were prepared by reactive melt infiltration and evaluated by gas- entrained solid particle impingement test Evolutions of microstructure morphology and elementphase distribution before and after erosion were mainly investigated to reveal the mechanism 2 Experimental procedure 21 Composites preparation Porous skeletons with size of 12 mmtimes12 mmtimes 12 mm were cut from a bulk CC composite which was thermal gradient chemical vapor infiltrated 25D needle punched fabric Densities of the fabric before and after infiltration of pyrocarbon were 045 and 095 gcm3 respectively The cut skeletons were cleaned in distilled water for 05 h by ultrasonic wave and then dried at 100 degC for 24 h Meanwhile mixed powders of Si and Al with different ratios were prepared by ball milling for 1minus2 h The Si powder was 45minus55 μm and the Al powder was 80minus120 μm Then the CC skeletons were embedded into the powder mixtures in a graphite crucible and heat treated at 1100minus1200 degC for 1minus3 h in 10minus2 Pa vacuum After furnace cooling the Si-Al infiltrated CC composites were taken out from the crucible and hand-abraded with 80 and 400 grit SiC papers to remove the surface adhered powders and reacted phases Finally samples with dimensions of 11 mmtimes11 mmtimes11 mm were hand-

polished by 400 grit SiC papers for test 22 Tests and characterization The density of the prepared composite was determined by drainage according to Archimedean principle The erosion test was performed at room temperature in a gas-blast device which was manufactured according to ASTM G76-2007 The main parameters are listed in Table 1 and the test is illustrated in Figure 1 Compressed air-entrained 50minus115 μm angular Al2O3+5 wt iron-oxide particles were accelerated in an alundum nozzle tube and then sprayed from the end of the nozzle and impinged vertically to the sample surface for 20 s from 10 mm distance The impinging stream was parallel to the web and non woven layer as shown in Figure 1 Inner diameter and length of the nozzle tube were 3 and 100 mm respectively Pressure of the air was 04 MPa and the particle feed rate was 600 mgs The particle impact velocity was 70 ms which was measured by the rotating double-disk method The linear and mass erosion rates were calculated according to Eqs (1) and (2)

l =d

Rt

(1)

m =m

Rt

(2)

where Rl is linear erosion rates Δd is the change of the samplersquos thickness at centre region before and after erosion Rm is the mass erosion rate Δm is the change of the mass before and after erosion t is erosion time The samples were measured and weighed at the accuracies of 1 μm and 01 mg respectively The phase analyses of the prepared composite were conducted by X-ray diffraction (XRD XrsquoPert Pro MPD) Morphology and chemical composition were investigated by scanning electron microscopy (SEM JSM6460) combined with energy dispersive spectroscopy (EDS) Table 1 Key parameters of erosion test

Parameter Value

Carrier air pressureMPa 04

Nozzle lengthmm 100

Inner diameter of nozzlemm 3

Al2O3 particle flux(mgsminus1) 600

Distance from nozzle end to samplemm 10

Impact angle(deg) 90

Impact velocity(msminus1) 70

Test durations 20


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2012 12 96minus108 DOI 101007s11668-011-9531-3


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S0008-6223(99)00125-6






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2012 12 96minus108 DOI 101007s11668-011-9531-3


中文导读







2562




(d) CC-SiC-50Al


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144956 DOI 101016japsusc2019144956





jwear2019203147





S0008-6223(99)00125-6






101016jcarbon200901045









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859minus865 DOI 101016 jwear201103029




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2012 12 96minus108 DOI 101007s11668-011-9531-3


中文导读







2563






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144956 DOI 101016japsusc2019144956





jwear2019203147





S0008-6223(99)00125-6






101016jcarbon200901045









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2012 12 96minus108 DOI 101007s11668-011-9531-3


中文导读







2564







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jwear2019203147





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101016jcarbon200901045









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859minus865 DOI 101016 jwear201103029




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S0008-6223(99)00125-6






101016jcarbon200901045









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859minus865 DOI 101016 jwear201103029




101016 jceramint201512124
























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2012 12 96minus108 DOI 101007s11668-011-9531-3


中文导读







2566

101016jjallcom201704188





jjallcom201708114




jtriboint201904010




144956 DOI 101016japsusc2019144956





jwear2019203147





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101016jcarbon200901045









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859minus865 DOI 101016 jwear201103029




101016 jceramint201512124
























201912059










2012 12 96minus108 DOI 101007s11668-011-9531-3


中文导读






Documents

Particle erosion of C/C-SiC composites with different Al