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The immersion end quenching method, combined with hardness testing, metallographic microscopy, scanning electron microscopy and transmission electron microscopy, was used to investigate the effect of quenching rate on the age hardening of 6061 aluminum alloy for building formwork. Results show that when the quenching rate decreases from 305 ℃/s to 26 ℃/s, the post-aging hardness of the alloy remains nearly unchanged. However, when the quenching rate drops below 26 ℃/s, the hardness decreases rapidly with further reduction in quenching rate. At quenching rates below 26 ℃/s, solute atoms precipitate from the supersaturated solid solution during cooling, forming β (Mg2Si) phases without strengthening effect at grain boundaries, Al13 (Fe, Cr)3Si2 dispersoids, and dislocations. This reduces the number of β″precipitates in the grains after aging, thereby lowering the alloy hardness. Lower quenching rates result in more β phases and lower post-aging hardness. It is concluded that the quenching rate shall exceed 26 ℃/s for attaining high hardness alloy.

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采用浸入式末端淬火方法,结合硬度测试、金相显微镜、扫描电镜和透射电镜等手段,研究了淬火速率对建筑模板用6061铝合金时效硬化行为的影响。结果表明:淬火速率从305 ℃/s减小至26 ℃/s时,合金时效后的硬度基本不变,淬火速度低于26 ℃/s时,合金硬度随着淬火速率降低而快速下降。淬火速率低于26 ℃/s时,过饱和固溶体在冷却过程中析出溶质原子,在晶界、Al13(Fe,Cr)3Si2弥散相及位错上形成无强化作用的β(Mg2Si)相,减少时效后晶内β″沉淀强化相数量,降低合金硬度。淬火速率越低,β相数量越多,时效后硬度越低。为了得到较高合金硬度,淬火速率需高于26 ℃/s。

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刘胜胆(1980—),男,江西吉水人,博士,教授,主要研究方向为轻质高强结构材料。E-mail:
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韦卫昌(1996—),男,广西南宁人,博士研究生,主要研究方向为高强铝合金性能调控。E-mail:

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韦卫昌(1996—),男,广西南宁人,博士研究生,主要研究方向为高强铝合金性能调控。E-mail:

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Mining and Metallurgical Engineering, 2023, 43(5): 149-153., articleTitle=Effect of interrupted quenching on microstructure and fracture toughness of 7N65 aluminum alloy, refAbstract=null), Reference(id=1241327688875561574, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241321695026409940, doi=null, pmid=null, pmcid=null, year=2017, volume=46, issue=9, pageStart=2553, pageEnd=2557, url=null, language=null, rfNumber=[18], rfOrder=25, authorNames=龙社明, 王孟君, 温柳, journalName=稀有金属材料与工程, refType=null, unstructuredReference=龙社明, 王孟君, 温柳, 等. 6082铝合金的淬火特性及微观组织[J]. 稀有金属材料与工程, 2017, 46(9): 2553-2557., articleTitle=6082铝合金的淬火特性及微观组织, refAbstract=null), Reference(id=1241327689051722346, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241321695026409940, doi=null, pmid=null, pmcid=null, year=2017, volume=46, issue=9, pageStart=2553, pageEnd=2557, url=null, language=null, rfNumber=[18], rfOrder=26, authorNames=LONG Sheming, WANG Mengjun, WEN Liu, journalName=Rare Metal Materials and Engineering, refType=null, unstructuredReference=LONG Sheming, WANG Mengjun, WEN Liu, et al. Quenching characteristics and microstructure of 6082 aluminum alloy[J]. 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(a)硬度-时效时间关系;(b)硬度-淬火速率关系

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(a)305 ℃/s;(b)12 ℃/s;(c)4 ℃/s

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(a)305 ℃/s;(b)12 ℃/s;(c)4 ℃/s;(d)第二相EDS分析结果

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(a)305 ℃/s;(b)12 ℃/s;(c)4 ℃/s;(d)弥散粒子的EDS结果

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(a)305 ℃/s;(b)12 ℃/s;(c)4 ℃/s;(d)SAED

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(a)305 ℃/s;(b)12 ℃/s;(c)4 ℃/s;(d)不同淬火速率下的PFZ宽度

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淬火速率对建筑模板用6061铝合金时效硬化行为的影响
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韦卫昌 1, 2 , 熊启臣 3 , 冯中进 3 , 樊磊 3 , 刘胜胆 1, 2 , 叶凌英 1, 2
矿冶工程杂志 | 材料 2025,45(2): 169-173
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矿冶工程杂志 | 材料 2025, 45(2): 169-173
淬火速率对建筑模板用6061铝合金时效硬化行为的影响
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韦卫昌1, 2 , 熊启臣3, 冯中进3, 樊磊3, 刘胜胆1, 2 , 叶凌英1, 2
作者信息
  • 1.中南大学 材料科学与工程学院,湖南 长沙 410083
  • 2.中南大学 有色金属材料科学与工程教育部重点实验室,湖南 长沙 410083
  • 3.云南爱家铝业有限公司,云南 曲靖 655335
  • 韦卫昌(1996—),男,广西南宁人,博士研究生,主要研究方向为高强铝合金性能调控。E-mail:

通讯作者:

刘胜胆(1980—),男,江西吉水人,博士,教授,主要研究方向为轻质高强结构材料。E-mail:
Effect of Quenching Rate on Age Hardening Behavior of 6061 Aluminum Alloy for Building Formwork
Weichang WEI1, 2 , Qichen XIONG3, Zhongjin FENG3, Lei FAN3, Shengdan LIU1, 2 , Lingying YE1, 2
Affiliations
  • 1.School of Materials Science and Engineering, Central South University, Changsha 410083, Hunan, China
  • 2.Key Laboratory of Nonferrous Metal Materials Science and Engineering, Ministry of Education, Central South University, Changsha 410083, Hunan, China
  • 3.Yunnan Aijia Aluminum Co., Ltd., Qujing 655335, Yunnan, China
出版时间: 2025-04-01 doi: 10.3969/j.issn.0253-6099.2025.02.030
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采用浸入式末端淬火方法,结合硬度测试、金相显微镜、扫描电镜和透射电镜等手段,研究了淬火速率对建筑模板用6061铝合金时效硬化行为的影响。结果表明:淬火速率从305 ℃/s减小至26 ℃/s时,合金时效后的硬度基本不变,淬火速度低于26 ℃/s时,合金硬度随着淬火速率降低而快速下降。淬火速率低于26 ℃/s时,过饱和固溶体在冷却过程中析出溶质原子,在晶界、Al13(Fe,Cr)3Si2弥散相及位错上形成无强化作用的β(Mg2Si)相,减少时效后晶内β″沉淀强化相数量,降低合金硬度。淬火速率越低,β相数量越多,时效后硬度越低。为了得到较高合金硬度,淬火速率需高于26 ℃/s。

淬火速率  /  6061铝合金  /  建筑模板  /  时效硬化  /  浸入式末端淬火  /  弥散强化  /  硬度

The immersion end quenching method, combined with hardness testing, metallographic microscopy, scanning electron microscopy and transmission electron microscopy, was used to investigate the effect of quenching rate on the age hardening of 6061 aluminum alloy for building formwork. Results show that when the quenching rate decreases from 305 ℃/s to 26 ℃/s, the post-aging hardness of the alloy remains nearly unchanged. However, when the quenching rate drops below 26 ℃/s, the hardness decreases rapidly with further reduction in quenching rate. At quenching rates below 26 ℃/s, solute atoms precipitate from the supersaturated solid solution during cooling, forming β (Mg2Si) phases without strengthening effect at grain boundaries, Al13 (Fe, Cr)3Si2 dispersoids, and dislocations. This reduces the number of β″precipitates in the grains after aging, thereby lowering the alloy hardness. Lower quenching rates result in more β phases and lower post-aging hardness. It is concluded that the quenching rate shall exceed 26 ℃/s for attaining high hardness alloy.

quenching rate  /  6061 aluminum alloy  /  building formwork  /  age hardening  /  immersion end quenching  /  dispersion strengthening  /  hardness
韦卫昌, 熊启臣, 冯中进, 樊磊, 刘胜胆, 叶凌英. 淬火速率对建筑模板用6061铝合金时效硬化行为的影响. 矿冶工程杂志, 2025 , 45 (2) : 169 -173 . DOI: 10.3969/j.issn.0253-6099.2025.02.030
Weichang WEI, Qichen XIONG, Zhongjin FENG, Lei FAN, Shengdan LIU, Lingying YE. Effect of Quenching Rate on Age Hardening Behavior of 6061 Aluminum Alloy for Building Formwork[J]. Mining and Metallurgical Engineering, 2025 , 45 (2) : 169 -173 . DOI: 10.3969/j.issn.0253-6099.2025.02.030
铝模板具有质量轻、强度高、施工方便、拼缝少、可回收等诸多优点,近年来大量应用于建筑领域[1-2]。6XXX系(Al-Mg-Si)铝合金是可热处理强化合金,时效后强度高,同时还具有优异的可挤压性能和耐腐蚀性能等[3-4],非常适用于生产铝模板。淬火是6XXX系铝模板生产过程的一个关键工序。为了保证时效后高的强度与硬度,需要对铝合金模板进行快速冷却[5],将Mg、Si等合金化元素“冻结”在铝基体中,在后续时效时获得多而弥散的沉淀强化相[6];但是过快的冷却容易导致铝合金模板翘曲甚至变形[7],降低成品率。因此,研究并确定6XXX系铝模板的临界淬火速率至关重要。本文针对一种6061铝合金模板,采用浸入式末端淬火方法获得大范围连续变化的淬火速率[8],研究淬火速率对时效硬化行为的影响规律,结合金相显微镜、扫描电镜和透射电镜的微观组织表征分析其影响机理,以确定临界淬火速率。研究结果可为铝模板实际生产时淬火介质的选择及工艺优化提供参考。
从6061铝合金模板上切取长125 mm、宽20 mm、厚6 mm的试样,其化学成分(质量分数,%)为:Al-0.95Mg-0.65Si-0.23Cu-0.31Fe-0.18Cr-0.08Mn。将试样置于SX-4-10型箱式电阻炉进行540 ℃/2 h固溶处理,然后迅速将试样一端浸入室温水(约25 ℃)中进行末端淬火,入水深度为25 mm,其余部分位于空气中。待试样完全冷却至室温后,立即在SX2-9-12TP箱式电阻炉中进行175 ℃人工时效。为获得不同位置的淬火速率,另取一块相同尺寸试样进行末端淬火,先在图1(a)所示不同位置沿横向(TD)钻出直径1.5 mm、深10 mm的小孔预埋热电偶,采集时间-温度曲线,数据采集频率为20 Hz。图1(b)为不同位置的时间-温度曲线。
6061铝合金的淬火敏感温度区间为230~450 ℃,在此区间淬火速率对其力学性能有显著影响[9]。据图1(b)计算了不同位置在该区间的淬火速率,结果如图2所示。由此可知,沿ED方向,随着距离增加,淬火速率从305 ℃/s快速减小到26 ℃/s,而后在30~120 mm范围内缓慢减小到4 ℃/s。
采用200HVS-5维氏硬度计测试时效后试样不同位置处的硬度,载荷为0.5 kg,保载时间为10 s,每个位置沿TD方向测试3个值,取平均值。金相试样经粗磨、细磨及机械抛光,在20%(体积分数)HF+80%(体积分数)蒸馏水试剂中浸蚀,然后在Leica DM2700M型金相显微镜上观察晶粒组织形貌。试样经机械抛光后,采用ZEISS MA10扫描电镜(SEM)观察第二相特征,采用Oxford EDS型能谱仪(EDS)分析第二相化学成分。试样先磨成厚度约80 μm的薄片,冲成直径3 mm的圆片后进行电解双喷减薄,使用液氮将温度控制在-20 ℃以下,双喷液成分为:30%(体积分数)HNO3+70%(体积分数)CH3OH,使用Titan G 260-300型扫描透射电镜(TEM)在明场像(BF)模式下观察试样中析出相形貌,并对第二相进行EDS分析和选区电子衍射(SAED)分析,加速电压为300 kV。
末端淬火试样不同淬火速率下的硬度与时效时间的关系曲线见图3(a)。不同淬火速率下的硬度均在时效时间0~2 h内快速上升,而后缓慢上升,约8~10 h达到最高值,然后随着时间延长缓慢下降。淬火速率305 ℃/s和26 ℃/s时的硬度相差不大;其他淬火速率下,淬火速率越小,硬度越低。为了更清楚地反映淬火速率对合金硬度的影响,给出了淬火速率与T6态(175 ℃/10 h)合金硬度的关系曲线,见图3(b)。淬火速率305 ℃/s时的硬度最高,为121.2HV;淬火速率减小至约26 ℃/s时,硬度基本不变;淬火速率低于26 ℃/s时,硬度随着淬火速率减小而快速下降,4 ℃/s时硬度仅109.8HV。据此,选择淬火速率305、12、4 ℃/s时的试样进行微观组织表征。
图4为不同淬火速率下末端淬火试样的金相组织照片。淬火速率305、12、4 ℃/s时的晶粒均呈等轴状,其尺寸相差不大,分别为111.8±59.3、107.8±59.3、(109.7±45.9)μm。305、12 ℃/s时试样中晶界清晰,不同晶粒的衬度较均匀;4 ℃/s试样中晶界也很清晰,但不同晶粒的衬度差别较大,晶粒内部有更多黑点。
图5为不同淬火速率试样的SEM照片及第二相的EDS分析结果。淬火速率305、12、4 ℃/s时,不同试样中都有许多白色的微米级第二相,其特征差别不大,面积分数分别为(0.52±0.05)%、(0.47±0.05)%和(0.49±0.07)%,尺寸分别为2.12±0.98、2.03±0.78、(2.06±0.87)μm。EDS分析结果表明这些第二相的化学成分相近,主要含有Al、Fe和Si元素,典型结果如图5(d)所示,其中Fe和Si的原子比接近1∶1,表明其为AlFeSi相[10]。
采用透射电镜对试样微观组织特征进行进一步观察和分析,结果如图67所示。由图6可见,305 ℃/s试样中能看到一些尺寸80~200 nm的亚微米近球状弥散粒子,典型的能谱结果见图6(d)。该粒子中除了Al元素外,还含有5.5%Fe、4.9%Si、2.5%Cr(原子分数)以及少量的Mg和Mn元素,根据以往研究可知,这应该是Al13(Fe,Cr)3Si2弥散相[11]。由图7可见,在更高倍数下观察到晶粒内部分布着高密度的纳米级沉淀强化相,沿(100)Al方向的SAED如图7(d)所示,1/2{220}位置附近的“十字斑”表明这些沉淀强化相是β″相[12]
图6(b)、(c)可知,12 ℃/s试样和4 ℃/s试样中除了近球形弥散粒子,还能观察到一些长棒状的β(Mg2Si)第二相,它们大都和弥散粒子结合在一起,见图7(b)、(c)。12 ℃/s试样中,近球状弥散粒子上有尺寸较小的β相(图7(b));靠近它们周围的铝基体中沉淀强化相的数量明显更少,衬度更亮。4 ℃/s试样中的β相数量更多(图6(c)),尺寸更大(图7(c));图中近球状弥散粒子尺寸约200 nm,棒状β相长度约420 nm,宽度约40 nm。另外,在一些区域还能看到呈链状分布的黑色粒状β相,尺寸5~20 nm,它们周围的沉淀强化相数量更少,衬度更白,如图7(d)中箭头所指;这种现象在12 ℃/s试样中很少观察到。据其特征和相关文献[5,13],这些黑色的粒状β相是在缓慢冷却过程中于位错上形核并长大的。
图8为不同淬火速率下试样晶界处的高倍TEM形貌照片。从图8可知,305 ℃/s试样晶界上分布着断续的短棒状黑色β相,长度约100 nm,宽度约35 nm,晶界附近没有β″沉淀强化相,形成了一条明显的亮色无沉淀析出带(PFZ),其宽度约70 nm。淬火速率减小到12 ℃/s,试样晶界上的β相尺寸增大,长度约为110 nm,宽度约为50 nm,PFZ宽度增至约180 nm。4 ℃/s试样晶界上的β相尺寸更大,长度约230 nm,宽度约40 nm,PFZ宽度进一步增加,约为240 nm。对试样中多个晶界的PFZ宽度进行测量计算平均值,结果如图8(d)所示,可见晶界PFZ宽度随着淬火速率减小而增加。
6XXX系铝合金是可热处理强化合金,时效后在晶内形成的高密度纳米级β″相能有效阻碍塑性变形时位错的运动,提高合金强度和硬度[14]。β″相的数量越多,强化效果越好,合金硬度越高。6061铝合金固溶后,Mg和Si元素都溶解于Al基体中;淬火速率高于26 ℃/s时,Mg和Si元素都保留在基体中形成高过饱和度固溶体,后续时效析出的β″相数量最多(图7(a)),因此,这些试样的硬度很高,如图3所示。
淬火速率减小时,固溶体发生分解,在弥散粒子、晶界及位错等位置形成了一些尺寸较大、强化作用较小的β相(图67)。晶界的界面能高,缓慢冷却时往往最先成为第二相非均匀形核的位置[15]。缓慢冷却时,Mg和Si原子扩散至晶界而形成β相,它们在后续时效时具有尺寸优势,可吸收周围的溶质原子而继续长大,因此尺寸较快速冷却时的尺寸更大。缓慢冷却不仅能降低晶界附近的溶质原子,还能降低空位浓度[16-17],这导致时效时晶界附近大范围难以形成β″沉淀强化相,出现无沉淀析出带。这些无沉淀析出带更软,不利于硬度的提高。此外,亚微米级的Al13(Fe,Cr)3Si2弥散粒子与铝基体之间往往是高能的非共格界面[5],缓慢冷却时也能充当第二相非均匀形核位置而导致粗大β相析出(图7)。β相的形成降低了其附近基体中Mg和Si原子浓度,导致时效时β″沉淀强化相难以形核析出[18],因此数量减少,不利于硬度的提高。淬火速率更低时,位错上形成了β相(图7(c)),虽然尺寸较小,但比β″沉淀强化相尺寸大,强化效果较低。综上所述,缓慢冷却过程中只要形成了β相,必然就减少了时效后纳米级β″沉淀强化相的数量,最终降低合金硬度。
淬火速率越小,在淬火敏感温度区间停留的时间越长(图1(b)),更多的Mg和Si溶质原子能扩散至β相而促使其长大,因而损失的溶质原子数量更多,导致时效后形成的β″沉淀强化相数量更少,最终试样硬度更低。因此,淬火速率低于26 ℃/s时,合金硬度随着淬火速率减小而不断降低。为了抑制β相的析出,得到较高的硬度,淬火速率应不低于26 ℃/s;但淬火速率也不宜过高,否则将导致合金中残余应力过大并发生合金翘曲变形。
1)淬火速率从305 ℃/s减小至26 ℃/s时,合金时效后硬度基本不变;淬火速率低于26 ℃/s时,硬度随着淬火速率减小而快速减小。为保证合金具有较高硬度,淬火速率应不低于26 ℃/s。
2)淬火速率低于26 ℃/s时,过饱和固溶体开始发生分解,于晶界和弥散粒子处形成粗大且无强化效果的β相,时效后其周围产生宽且软的PFZ,减少了β″沉淀强化相的数量,降低了合金硬度;淬火速率减小至4 ℃/s时,β相尺寸增大,而且还在位错上析出,进一步降低了合金硬度。
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2025年第45卷第2期
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doi: 10.3969/j.issn.0253-6099.2025.02.030
  • 接收时间:2024-10-10
  • 首发时间:2026-03-19
  • 出版时间:2025-04-01
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  • 收稿日期:2024-10-10
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云南省科技人才与平台计划项目(202205AF150045)
作者信息
    1.中南大学 材料科学与工程学院,湖南 长沙 410083
    2.中南大学 有色金属材料科学与工程教育部重点实验室,湖南 长沙 410083
    3.云南爱家铝业有限公司,云南 曲靖 655335

通讯作者:

刘胜胆(1980—),男,江西吉水人,博士,教授,主要研究方向为轻质高强结构材料。E-mail:
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2种不同金属材料的力学参数

Family
属数
Number of
genus
种数
Number of
species
占总种数比例
Percentage of
total species (%)

Genus
种数
Number of
species
占总种数比例
Percentage of total
species (%)
鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
小菇科 Mycenaceae 2 12 5.74 丝盖伞属 Inocybe 5 2.39
多孔菌科 Polyporaceae 8 14 6.70 蜡蘑属 Laccaria 5 2.39
红菇科 Russulaceae 3 23 11.00 小皮伞属 Marasmius 6 2.87
小菇属 Mycena 11 5.26
光柄菇属 Pluteus 5 2.39
红菇属 Russula 17 8.13
栓菌属 Trametes 5 2.39
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