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Article(id=1240631741593997541, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631729627648823, articleNumber=null, orderNo=null, doi=10.3969/j.issn.0253-6099.2024.03.030, pmid=null, cstr=null, oa=null, hot=null, price=null, onlineType=0, articleFormat=0, articleType=null, articleTypeStr=null, receivedDate=1701014400000, receivedDateStr=2023-11-27, revisedDate=null, revisedDateStr=null, acceptedDate=null, acceptedDateStr=null, onlineDate=1773719257019, onlineDateStr=2026-03-17, pubDate=1717171200000, pubDateStr=2024-06-01, doiRegisterDate=null, doiRegisterDateStr=null, onlineIssueDate=1773719257019, onlineIssueDateStr=2026-03-17, onlineJustAcceptDate=null, onlineJustAcceptDateStr=null, onlineFirstDate=null, onlineFirstDateStr=null, sourceXml=null, magXml=null, createTime=1773719257019, creator=13701087609, updateTime=1773719257019, updator=13701087609, issue=Issue{id=1240631729627648823, tenantId=1146029695717560320, journalId=1235980550691926019, year='2024', volume='44', issue='3', pageStart='1', pageEnd='181', issueExtLink='null', onlineDate='null', pubDate='null', beforeIssueId=null, nextIssueId=null, price=null, status=1, issueComplete=1, articleOrder=1, issueType=-1, specialIssue=null, createTime=1773719254166, creator=13701087609, updateTime=1773724083554, updator=13701087609, preIssue=null, nextIssue=null, ext={EN=IssueExt(id=1240651985603580488, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631729627648823, language=EN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=), CN=IssueExt(id=1240651985603580489, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631729627648823, language=CN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=)}, issueFiles=null}, startPage=140, endPage=144, ext={EN=ArticleExt(id=1240631743284302095, articleId=1240631741593997541, tenantId=1146029695717560320, journalId=1235980550691926019, language=EN, title=Effect of Ion Nitriding on Microstructure and Friction and Wear Property of 38CrMoAl Steel, columnId=1236276108207902848, journalTitle=Mining and Metallurgical Engineering, columnName=MATERIALS, runingTitle=null, highlight=null, articleAbstract=

The surface of 38CrMoAl steel was processed by ion nitriding at 560 ℃ with the mixture of nitrogen and argon as nitrogen source. After that, the friction and wear property of 38CrMoAl steel was studied. The results show that as the N2 volume fraction in the mixed gas increases, the thickness of nitrided layer increases, and the surface hardness of the nitrided layer increases first and then decreases. By adjusting the volume fraction of N2 in the mixed gas, the number of active nitrogen atoms can be changed, thus leading to the change in the phase composition of the nitrided layer. With N2 and Ar in a volume ratio of 2∶3, γ′-Fe4N phase is the major phase and ε-Fe2-3N phase is the minor phase in the nitrided sample. With N2 and Ar in a volume ratio of 3∶2, the nitrided layer has ε-Fe2-3N phase as the major phase andγ′-Fe4N as the minor phase. Compared with the substrate material, the ion-nitrided sample has a smaller friction coefficient and higher wear-resistance. With N2 and Ar in a volume ratio of 3∶2, the ion-nitrided sample has its compound layer in a thickness of 21.4 μm, and its average friction coefficient up to 0.26, presenting good wear resistance. The mechanisms of friction and wear include fatigue, abrasion and oxidation.

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560 ℃下，以氮气和氩气的混合气体为氮源，对38CrMoAl钢表面进行离子渗氮，研究了离子渗氮后38CrMoAl钢的磨擦磨损性能。结果表明，随着混合气体中N2体积分数增大，渗氮层厚度增加，渗氮层表面硬度呈现先增大后减小的趋势。通过调节混合气体中N2的体积分数，可以改变活性氮原子数量从而改变渗氮层的物相组成，当N2和Ar体积比2∶3时，渗氮层中以γ′-Fe4N相为主相、ε-Fe2-3N相为次相；当N2和Ar体积比3∶2时，渗氮层中ε-Fe2-3N相成为主相、γ′-Fe4N相为次相。与基体材料相比，离子渗氮试样具有更小的摩擦系数，耐磨性得到提高，在N2和Ar体积比3∶2时，渗氮试样的化合物层厚度为21.4 μm，平均摩擦系数达到0.26，表现出良好的耐磨性。摩擦磨损机制为疲劳磨损、磨粒磨损和氧化磨损。

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刘俊伟（1981—），男，甘肃兰州人，博士，副教授，主要从事镁铝合金、表面工程研究。E-mail：
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王紫阳（1999—），男，河北武安人，硕士研究生，主要从事表面改性强化研究。E-mail：

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王紫阳（1999—），男，河北武安人，硕士研究生，主要从事表面改性强化研究。E-mail：

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王紫阳（1999—），男，河北武安人，硕士研究生，主要从事表面改性强化研究。E-mail：

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language=CN, orderNo=5, keyword=化合物层), Keyword(id=1240651348677546919, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=CN, orderNo=6, keyword=耐磨性), Keyword(id=1240651348925010872, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=CN, orderNo=7, keyword=磨粒磨损), Keyword(id=1240651349197640651, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=CN, orderNo=8, keyword=氧化磨损)], refs=[Reference(id=1240651352012017939, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, doi=null, pmid=null, pmcid=null, year=2017, volume=145, issue=null, pageStart=153, pageEnd=157, url=null, language=null, rfNumber=[1], rfOrder=0, authorNames=LU S J, MIAO B, SONG L, journalName=Vacuum, refType=null, unstructuredReference=LU S J, MIAO B, SONG L, et al. 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（a）N2∶Ar=2∶3；（b）N2∶Ar=3∶2；（c）N2∶Ar=4∶1

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（a）调质钢；（b）不同氮氩气体比例下离子渗氮

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（a）调质钢；（b）N2∶Ar=2∶3离子渗氮；（c）N2∶Ar=3∶2离子渗氮；（d）N2∶Ar=4∶1离子渗氮

, figureFileSmall=spsKb6qKpI+31W0A1cc7lg==, figureFileBig=khQjcJHSaTMOLWfJjtCoPw==, tableContent=null), ArticleFig(id=1240651350493679724, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=EN, label=null, caption=null, figureFileSmall=70RqJzQPIUwbq/tk7q8y7A==, figureFileBig=wcmZiEm/Z5IgNgiVD9i60Q==, tableContent=null), ArticleFig(id=1240651350602731640, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=CN, label=图5, caption=不同氮气氩气比例等离子氮化后试样的磨损形貌

（a）N2∶Ar=2∶3；（b）N2∶Ar=3∶2

, figureFileSmall=70RqJzQPIUwbq/tk7q8y7A==, figureFileBig=wcmZiEm/Z5IgNgiVD9i60Q==, tableContent=null), ArticleFig(id=1240651350741143687, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=EN, label=null, caption=null, figureFileSmall=Gy6+exw1BVhVoLVXtlpwow==, figureFileBig=bMluh+iys6eOeWIkGklvzw==, tableContent=null), ArticleFig(id=1240651350892138647, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631741593997541, language=CN, label=图6, caption=38CrMoAl钢试样渗氮层磨损表面SEM图

（a）N2∶Ar=2∶3；（b）N2∶Ar=3∶2

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CMnCrMoSiAlFe
0.380.451.640.180.350.90余量
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38CrMoAl钢基体化学成分（质量分数）

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CMnCrMoSiAlFe
0.380.451.640.180.350.90余量
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区域CNOAlCrFe
18.934.9826.360.632.3056.80
27.765.2221.210.406.6358.79
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图6中相关区域的EDS测试结果（质量分数）

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区域CNOAlCrFe
18.934.9826.360.632.3056.80
27.765.2221.210.406.6358.79
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离子渗氮对38CrMoAl钢组织及摩擦磨损性能影响
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王紫阳 , 刘俊伟 , 罗佳杰 , 刘振亚 , 李嘉成
矿冶工程杂志 | 材料 2024,44(3): 140-144
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矿冶工程杂志 | 材料 2024, 44(3): 140-144
离子渗氮对38CrMoAl钢组织及摩擦磨损性能影响
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王紫阳 , 刘俊伟 , 罗佳杰, 刘振亚, 李嘉成
作者信息
  • 南昌航空大学　材料科学与工程学院，江西　南昌　330063

    • 王紫阳（1999—），男，河北武安人，硕士研究生，主要从事表面改性强化研究。E-mail：

通讯作者:

刘俊伟（1981—），男，甘肃兰州人，博士，副教授，主要从事镁铝合金、表面工程研究。E-mail：
Effect of Ion Nitriding on Microstructure and Friction and Wear Property of 38CrMoAl Steel
Ziyang WANG , Junwei LIU , Jiajie LUO, Zhenya LIU, Jiacheng LI
Affiliations
  • School of Materials Science and Engineering, Nanchang Hangkong University, Nanchang 330063, Jiangxi, China
出版时间: 2024-06-01 doi: 10.3969/j.issn.0253-6099.2024.03.030
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摘要
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560 ℃下，以氮气和氩气的混合气体为氮源，对38CrMoAl钢表面进行离子渗氮，研究了离子渗氮后38CrMoAl钢的磨擦磨损性能。结果表明，随着混合气体中N2体积分数增大，渗氮层厚度增加，渗氮层表面硬度呈现先增大后减小的趋势。通过调节混合气体中N2的体积分数，可以改变活性氮原子数量从而改变渗氮层的物相组成，当N2和Ar体积比2∶3时，渗氮层中以γ′-Fe4N相为主相、ε-Fe2-3N相为次相；当N2和Ar体积比3∶2时，渗氮层中ε-Fe2-3N相成为主相、γ′-Fe4N相为次相。与基体材料相比，离子渗氮试样具有更小的摩擦系数，耐磨性得到提高，在N2和Ar体积比3∶2时，渗氮试样的化合物层厚度为21.4 μm，平均摩擦系数达到0.26，表现出良好的耐磨性。摩擦磨损机制为疲劳磨损、磨粒磨损和氧化磨损。

表面处理  /  38CrMoAl钢  /  离子渗氮  /  氮氩比  /  化合物层  /  耐磨性  /  磨粒磨损  /  氧化磨损

The surface of 38CrMoAl steel was processed by ion nitriding at 560 ℃ with the mixture of nitrogen and argon as nitrogen source. After that, the friction and wear property of 38CrMoAl steel was studied. The results show that as the N2 volume fraction in the mixed gas increases, the thickness of nitrided layer increases, and the surface hardness of the nitrided layer increases first and then decreases. By adjusting the volume fraction of N2 in the mixed gas, the number of active nitrogen atoms can be changed, thus leading to the change in the phase composition of the nitrided layer. With N2 and Ar in a volume ratio of 2∶3, γ′-Fe4N phase is the major phase and ε-Fe2-3N phase is the minor phase in the nitrided sample. With N2 and Ar in a volume ratio of 3∶2, the nitrided layer has ε-Fe2-3N phase as the major phase andγ′-Fe4N as the minor phase. Compared with the substrate material, the ion-nitrided sample has a smaller friction coefficient and higher wear-resistance. With N2 and Ar in a volume ratio of 3∶2, the ion-nitrided sample has its compound layer in a thickness of 21.4 μm, and its average friction coefficient up to 0.26, presenting good wear resistance. The mechanisms of friction and wear include fatigue, abrasion and oxidation.

surface treatment  /  38CrMoAl steel  /  ion nitriding  /  ratio of nitrogen to argon  /  compound lay  /  wear resistance  /  abrasive wear  /  oxidation wear
王紫阳, 刘俊伟, 罗佳杰, 刘振亚, 李嘉成. 离子渗氮对38CrMoAl钢组织及摩擦磨损性能影响. 矿冶工程杂志, 2024 , 44 (3) : 140 -144 . DOI: 10.3969/j.issn.0253-6099.2024.03.030
Ziyang WANG, Junwei LIU, Jiajie LUO, Zhenya LIU, Jiacheng LI. Effect of Ion Nitriding on Microstructure and Friction and Wear Property of 38CrMoAl Steel[J]. Mining and Metallurgical Engineering, 2024 , 44 (3) : 140 -144 . DOI: 10.3969/j.issn.0253-6099.2024.03.030
正文
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液压泵柱塞、轴承、齿轮等部件使用环境越来越复杂，要求材料的表面性能不断提高[1]。为了提高材料的表面性能，常对其进行离子渗氮处理[2-4]。离子渗氮技术是通过辉光放电将阴极与阳极间的含氮气氛电离成含氮离子的等离子体，在电场作用下向试样表面加速轰击，与试样溅射出的原子形成氮化物沉积在试样表面，并在持续沉积与反应下生成氮化层。但离子渗氮技术存在渗氮速度慢、渗氮层质量较差等一系列缺陷，并且对试样进行高温或长时间离子渗氮时会影响渗氮层质量，从而降低渗氮层性能[5-6]。
为了进一步提高渗氮速度和渗氮层质量，学者们对离子渗氮工艺参数如渗氮温度[7-8]、渗氮时间[9-10]、渗氮气体[11-12]、炉内气压[13-14]等进行了研究。在离子渗氮中，大部分研究都是以氮氢混合气体或氨气作为氮源[15-16]，极少以氮氩混合气体作为氮源。本文在较高渗氮温度下以38CrMoAl钢为基体，采用氩气和氮气的混合气体进行表面离子渗氮，研究离子渗氮后38CrMoAl钢的摩擦磨损行为，结合化合物层厚度、硬度及相组成，分析试样耐磨性提高的原因，揭示离子渗氮试样的磨损机理。
1　实验材料及方法
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1.1　实验材料
实验材料为38CrMoAl钢，其化学成分如表1所示，对其进行调质处理后，测得其表面硬度为360HV0.1。利用线切割机将试样加工成10 mm×10 mm×5 mm的立方体，再依次用400～2 000目SiC砂纸进行研磨，然后抛光至镜面，放入无水乙醇中进行超声波清洗，吹干待用。
1.2　实验方法与检测
采用JSD500型多功能离子渗氮炉，所用工作气体为氮气与氩气。将样品置于炉中，抽炉内气压至真空度6×10-4Pa。首先，通入氩气，在真空度10 Pa左右溅射清洗30 min，去除样品表面的天然钝化膜。清洗结束后，将氮气与氩气体积比分别控制在2∶3、3∶2和4∶1，其中氮氩混合气体总流量为500 mL/min、渗氮气压120 Pa、渗氮温度560 ℃、保温时间10 h，进行离子渗氮处理。离子渗氮处理结束后，将样品在氮气气氛中缓慢冷却至室温后取出。
采用显微硬度仪测量试样表面硬度与截面硬度，载荷为100g，保载时间15 s；将渗氮后的试样打磨抛光后，用4%硝酸酒精溶液进行腐蚀，并通过金相显微镜观察试样截面组织；使用D8ADVANCE-A25型X射线衍射仪对试样表面进行物相分析，扫描角度设置范围为20°～80°，靶材选为Cu靶。使用HT-1000型号磨损试验机测试试样耐磨性，选用半径2 mm的GCr15钢球作为对磨材料，在200g载荷下以转速200 r/min、旋转半径2 mm与渗氮试样旋转对磨30 min；使用FEI Nova Nano SEM450型扫描电子显微镜观察样品磨痕的微观形貌并进行EDS测试。
2　实验结果与分析
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2.1　合金渗氮后的组织和XRD图谱
38CrMoAl钢在不同N2和Ar体积比下离子渗氮处理后的截面金相显微组织如图1所示。不同气体比例下离子渗氮后试样表层都生成了白亮层。在N2和Ar体积比分别为2∶3、3∶2、4∶1时，渗氮层厚度分别为248.3 μm、388.3 μm、455.2 μm，化合物层厚度分别为9.8 μm、21.4 μm、13.7 μm。可见，随着渗氮气氛中氮气比例增加，渗氮层厚度也逐渐增加。由此可见，温度一定时，通过增加渗氮气氛中氮气比例可以提高渗氮层厚度，加快渗氮速度。由于氮的化学键强度（9.67 eV）高于其他分子，在电离时会受到其他分子的限制影响[17]。本实验加入氩气使得38CrMoAl钢可以在更短的时间内生成厚度更大的渗氮层，大幅度提高了渗氮速度，说明氩气可以使氮气电离时所需的能量降低，提高氮气的电离效率，使得参与反应的活性氮原子数量上升；另一方面，氩气电离出的氩离子会加速轰击试样表面，使试样表面产生缺陷并成为氮离子向试样内部扩散的通道；在两种效应的共同作用下，离子渗氮的速度得到了大幅度提高。
图2为38CrMoAl钢试样调质处理及渗氮处理后的X射线衍射图谱。由图2可以看出，调质钢全由α-Fe相组成，没有残余的奥氏体相；不同N2和Ar体积比下离子渗氮处理后，试样表面的主要物相由α-Fe相转变为ε-Fe2-3N相和γ′-Fe4N相[18]。
N2和Ar体积比为2∶3时，渗氮层中以γ′-Fe4N相为主相、ε-Fe2-3N相为次相。随着渗氮气氛中N2比例提高，ε-Fe2-3N相开始成为主相，次相为γ′-Fe4N相。这是由于氮与铁的反应属于反应扩散，铁氮化合物的生成与氮含量有关[19]。由Fe-N相图可知，ε-Fe2-3N化合物中的氮含量高于γ′-Fe4N化合物。随着混合气体中氮气比例上升，炉中会有更多氮原子与基体中溅射出的铁原子发生反应，提高了铁氮化合物中氮元素含量，生成更多的ε-Fe2-3N富氮化合物。由此说明，通过控制渗氮气氛中氮气比例，可以控制38CrMoAl钢渗氮层物相组成。
2.2　硬度梯度
不同N2和Ar体积比下制备的渗氮层显微硬度分布如图3所示。N2和Ar体积比2∶3、3∶2、4∶1时，离子渗氮试样表面硬度分别为950.3HV0.1、1 040.3HV0.1、998.2HV0.1。离子渗氮处理后试样表面硬度相对于基体都得到极大提高。但渗氮试样显微硬度从表面到基体不断下降，并逐渐接近基体调质钢的硬度。从图3可以看出，随着混合气体中氩气比例提高，渗氮层截面硬度得到提高，说明氩气的加入可以改善渗氮层中扩散层的性能，这是由于氩气含量较高时可以获得小间隙的均匀辉光放电，并能够更加稳定地电离氮气，提供数量稳定的活性氮原子，使氮元素向试样内部扩散更均匀，从而改善了扩散层性能。但N2和Ar体积比2∶3时，在距表面一定深度后试样截面硬度会低于N2和Ar体积比3∶2与4∶1的试样，这说明混合气体中氮气比例较低时，渗氮层厚度会下降，这与图1结果一致。
混合气体中氮气比例上升，渗氮层表面硬度呈现先增大后减小的趋势，这与γ′-Fe4N相转变为硬度较高的ε-Fe2-3N相有关（见图2（b））。
2.3　摩擦系数与磨痕形貌
图4为离子渗氮处理前后试样摩擦系数随时间的变化曲线。
摩擦磨损试验开始后，试样均会进入磨合阶段，经过一段时间后可获得稳定磨损的摩擦系数[20]。将稳定磨损的摩擦系数取平均值得到平均摩擦系数。调质钢基体的平均摩擦系数为0.33；N2和Ar体积比4∶1和2∶3时，试样表面平均摩擦系数约为0.30；N2和Ar体积比3∶2时，试样平均摩擦系数为0.26。离子渗氮后试样的表面平均摩擦系数均小于基体试样，说明离子渗氮后试样耐磨性均得到提高。
以氮气和氢气体积比1∶4混合气体作为氮源在38CrMoAl表面进行离子渗氮，相同条件下，试样表面摩擦系数为0.32[15]，说明氩气的加入可以提高渗氮层表面耐磨性并提高渗氮层厚度。
图5为N2和Ar体积比2∶3、3∶2时离子渗氮试样的磨痕形貌。磨痕宽度与载荷的大小有关，相同载荷下，试样表面的磨痕宽度可以反映试样的摩擦磨损性能。N2和Ar体积比2∶3的渗氮试样磨痕宽度约为476 μm，N2和Ar体积比3∶2的渗氮试样磨痕宽度约为354 μm，且表面磨损和破碎痕迹减少，表明后者具有更好的耐磨性能。试样耐磨性会随着化合物层厚度与ε-Fe2-3N相含量的提高而得到改善，这归功于ε-Fe2-3N相具有良好的摩擦磨损性能与较高的硬度[21]。此外在渗氮层表面存在孔洞，这是氮分子的析出造成的[22]。
图6为不同N2和Ar体积比下制备的渗氮层磨损表面微观形貌图，其中图6（b）和图6（d）分别为图6（a）和图6（c）的局部放大图。从图6可以看出，N2和Ar体积比2∶3和3∶2的渗氮样品摩擦磨损时，在沿着摩擦副滑动方向上均发生了浅层剥落。随着摩擦磨损进行，试样表面会因颗粒脱落形成小坑洞，造成试样表面局部应力集中[23]，坑洞周围不断产生扩展裂纹，最终发生疲劳破坏造成浅层剥落。而因疲劳破坏掉落的碎屑在摩擦副的运作下被研磨成了小颗粒（图6（b），图6（d）），说明试样表面在磨损过程中也发生了磨粒磨损。
N2和Ar体积比2∶3的渗氮试样表面剥落情况比N2和Ar体积比3∶2的渗氮试样更加严重，这是化合物层厚度与表面硬度的区别引起的。前者化合物层厚度薄和表面硬度低，在相同载荷下进行摩擦磨损时，化合物层会在较短时间内严重破碎，产生更多的碎屑，并在摩擦副接触面之间被磨成小颗粒，从而发生了更严重的磨粒磨损。这说明化合物层较厚且较硬时可以有效减少浅层剥落，减缓疲劳磨损和磨粒磨损的发生，从而提高试样的摩擦磨损性能。
表2为图6中相关区域的EDS测试结果。区域1与区域2均存在较高含量的O元素，这意味着渗氮试样在磨损过程中都发生了氧化磨损。
另外，区域2中Cr元素含量高于区域1，说明N2和Ar体积比3∶2的渗氮试样表面有更多Cr的氮化物生成。而Cr的氮化物具有很高的抵抗磨损能力，这也是该试样有更好耐磨性的原因[24]。
3　结论
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1）560 ℃下，以氮气和氩气的混合气体为氮源，对38CrMoAl钢表面进行离子渗氮，渗氮层厚度随N2体积分数增大而增加，N2和Ar体积比4∶1时，渗氮层厚度为455.2 μm；渗氮层表面硬度随着N2体积分数增大呈现先增大后减小的趋势，N2和Ar体积比3∶2时，渗氮层表面硬度达到1 040.3HV0.1。
2）通过调节混合气体中N2的比例，可以改变活性氮原子数量从而改变渗氮层的物相组成。N2和Ar体积比2∶3时，渗氮层中以γ′-Fe4N相为主相、ε-Fe2-3N相为次相；N2和Ar体积比3∶2和4∶1时，ε-Fe2-3N相成为主相，γ′-Fe4N相为次相。
3）与基体材料相比，离子渗氮试样具有更小的摩擦系数，耐磨性得到提高，摩擦磨损机制为疲劳磨损、磨粒磨损和氧化磨损。N2和Ar体积比3∶2时，渗氮试样化合物层厚度为21.4 μm，平均摩擦系数达到0.26，表现出良好的耐磨性。
基金
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  • 国家自然科学基金(51504138; 51674118)
  • 江西省教育厅科技基金(GJJ150726)
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2024年第44卷第3期
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doi: 10.3969/j.issn.0253-6099.2024.03.030
  • 接收时间：2023-11-27
  • 首发时间：2026-03-17
  • 出版时间：2024-06-01
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  • 收稿日期：2023-11-27
基金
国家自然科学基金(51504138; 51674118)
江西省教育厅科技基金(GJJ150726)
作者信息
    南昌航空大学　材料科学与工程学院，江西　南昌　330063

通讯作者:

刘俊伟（1981—），男，甘肃兰州人，博士，副教授，主要从事镁铝合金、表面工程研究。E-mail：
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2种不同金属材料的力学参数
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鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
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