CN107299303A - 一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法 - Google Patents
一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法 Download PDFInfo
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- CN107299303A CN107299303A CN201710710800.6A CN201710710800A CN107299303A CN 107299303 A CN107299303 A CN 107299303A CN 201710710800 A CN201710710800 A CN 201710710800A CN 107299303 A CN107299303 A CN 107299303A
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- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminum Chemical compound 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[Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N copper Chemical compound 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[Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N magnesium Chemical compound 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[Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 4
- 229910052712 strontium Inorganic materials 0.000 claims description 4
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium Chemical compound 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[Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N zinc Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- QCWXUUIWCKQGHC-UHFFFAOYSA-N zirconium Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 239000002893 slag Substances 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims 1
- 239000006104 solid solution Substances 0.000 abstract description 6
- 238000001125 extrusion Methods 0.000 abstract description 4
- 230000000052 comparative effect Effects 0.000 description 18
- 239000007787 solid Substances 0.000 description 16
- 230000001808 coupling Effects 0.000 description 15
- 238000010168 coupling process Methods 0.000 description 15
- 238000005859 coupling reaction Methods 0.000 description 15
- 238000005260 corrosion Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 6
- 239000000243 solution Substances 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
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- 238000004450 types of analysis Methods 0.000 description 3
- 238000005070 sampling Methods 0.000 description 2
- 238000004642 transportation engineering Methods 0.000 description 2
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- 238000005516 engineering process Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound 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- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 230000002035 prolonged Effects 0.000 description 1
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
Abstract
一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其特征是它主要包括：前处理和后续强化热处理。所述的前处理包括：一次热压缩；将经过一次热压缩的超高强铝合金加热至400℃，保温2h后，再放入模具中进行ECAP挤压处理；将经过ECAP挤压的超高强铝合金进行250±5℃×24h、300±5℃×6h和400±5℃×6h的预回复退火处理。所述的后续强化热处理包括：固溶、时效处理。使用本发明前处理方法处理的合金，再经过后续的固溶‑时效处理。本发明方法简单，操作方便，经本发明处理后的合金横向纵向塑性和各向同性得到显著提高，同时合金的其他各项性能也得以保持或提高。
Description
一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法
技术领域
[0001] 本发明是一种超高强铝合金横向纵向塑性及各向同性大幅提高的方法，具体地说 是一种综合利用热压缩、ECAP、预回复、固溶、时效技术来提高超高强铝合金塑性及各向同 性的方法。
背景技术
[0002] Al-Zn-Mg-Cu (7000)合金是一类重要的具有高强度、低密度及良好的热加工性能 等优点有合金材料，是航空航天领域首选的结构材料。近年来，在我国航空航天、武器装备 和交通运输的发展的推动下，7000系超高强铝合金也成为了研究的热点。但是该合金的不 足之处是脆性大，塑性差。
[0003] 为了满足不同条件下的使用要求，合金的塑性必须得到提高。合金成份的调整和 强化处理工艺的调整是提高合金性能的主要方法。等通道转角挤压简称ECAP，作为强烈塑 性变形方法的一种，相比于传统塑性变形方法，具有巨大的优势，在ECAP的作用下，合金的 晶体取向可以得到调整，并且ECAP会引入高密度的位错，使晶粒再结晶，促进晶粒等轴化和 晶体长大，有效地细化材料的内部结构，从而提高合金的塑性和各向同性。另一方面，ECAP 挤压过程材料几乎无变形，可以重复挤压。
[0004]迄今为止，尚未有一种具有自主知识广权的提尚超尚强错合金的横向纵向塑性和 各向同性的方法可供使用，在一定程度上制约了我国航空航天、武器装备和交通运输的发 展。因此结合提高7000系合金的几种主要方法改善该合金脆性大，塑性差，各向差异大的缺 点，对提尚超尚强错合金的塑性和各向同性具有重要的实际意义。
发明内容
[0005] 本发明的目的是针对现有的Al-Zn-Mg-Cu (7000)超高强铝合金塑性差和各向同性 差异大等的问题，发明一种提高超高强铝合金横向纵向塑性和各向同性的方法。
[0006] 本发明的技术方案是： 一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其特征在于它由前处理 和后处理组成，所述的前处理为依次进行的一次热压缩、等通道转角挤压和预回复处理，所 述的后处理为后续强化热处理。
[0007] 所述的一次热压缩是将超高强铝合金加热至400±5°C，保温2±0.5h后进行变形 量不小于50%的压缩变形。本发明的400 ± 5°C是指温度为395-405之间的任意温度，2 ±0.5h 是指1.5_2.5小时之间的任意时间，下同。
[0008] 所述的等通道转角挤压是将经过一次热压缩的超高强铝合金再次加热至400 ±5 。(：，保温2 ± 0.5h后放入模具中进行等通道转角挤压处理。
[0009] 4.根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方 法，其特征是所述的预回复处理是将经过等通道转角挤压处理的超高强铝合金进行250±5 °CX 24±lh、300±5°CX 6±lh和400±5°CX 6±1 h的预回复退火处理。
[0010] 所述的后续强化热处理为固溶处理+时效处理。
[0011 ] 所述的固溶处理是指对经过预处理的超高强错合金进行450 ± 5 °C X 2 ± 0.5h、460 ± 5 °C X 2 ± 0 · 5h和470 ± 5 °C X 2 ± 0 · 5h的强化固溶处理；所述时效处理是指将经过固溶处 理的超高强铝合金在常温下立即进行水淬，水淬温度为25±5°C，然后进行100°C X 6h〜48 h (梯度为6h)或120°CX6 h〜48 h(梯度为6h)的时效处理。
[0012] 所述的超高强铝合金为经过均质化处理的挤压态7000系(Al-Zn-Mg-Cu)合金，它 主要由铝(Al)、锌（Zn)、镁(Mg)、铜（Cu)、锆（Zr)、锶（Sr)组成，其中锌（Zn)的质量百分比 10 · 78〜13 · 01 %，镁(Mg)的质量百分比为2 · 78〜3 · 16%，铜（Cu)的质量百分比2 · 59〜2 · 8%，锆 (Zr)的质量百分比0.204〜0.22%，锶（Sr)的质量百分比0.047〜0.0757%，余量为铝和少量杂 质元素，各组份的质量百分比之和为100%。
[0013] 本发明的有益效果： (1)经本发明方法(热压缩-等通道转角挤压-预回复-固溶-时效)处理的合金，横向纵 向塑性及各向同性均提高。ECAP工艺可以调整晶体取向，引入高密度的位错，使晶粒再结 晶，促进晶粒等轴化和晶粒长大，从而提高合金塑性和各向同性。以实施例一为例，X方向的 延伸率由4.9%和5.1 %提高到了 10.5%，增长了 114.3%和105.9%; Y方向的延伸率由8.7%和 8.9%提高到了 11.1%，增长了 27.6%和24.7%，即X、Y方向（横向、纵向）的塑性得到显著提高。 同时经过热压缩-等通道转角挤压-预回复-固溶-时效处理的合金X、Y方向（横向、纵向）的 屈服强度和极限强度相差无几，表明实施例一的各向同性得到了提高，反而对比例一和对 比例二的Χ、Υ方向屈服强度和极限强度差异大，即各向同性较差。在实施例二中，Y方向的延 伸率从7.0%和6.8%提高到了 12.8%，增长了82.8%和88.2%左右，S卩Y向（纵向）塑性显著提高。
[0014] (2)经本发明方法(热压缩-等通道转角挤压-预回复-固溶-时效)处理的合金，合 金的其他部分性能得以保持或提高。
[0015] (3)本发明所述超高强铝合金横向纵向塑性及各向同性提高方法，操作简单，设备 要求低，具备很好的应用前景。
[0016] (4)本发明为后续提高超高强铝合金的塑性和各向同性的研究提供了参考。
附图说明
[0017] 图1是经过热压缩-等通道转角挤压-预回复-固溶-时效（120°CX48 h)处理后的 实施例一合金的X、Y、Z三个方向的金相照片。（a)X方向的金相照片；（b) Y方向的金相照片； (c) Z方向的金相照片。
[0018] 图2是经过热压缩-预回复-固溶-时效（120°CX48 h)处理后的对比例一合金的X、 Y、Z三个方向的金相照片。（a)X方向的金相照片；（b) Y方向的金相照片；（C) Z方向的金相 照片。
[0019] 图3是经过热压缩-固溶-时效（120°C X 48 h)处理后的对比例二合金的X、Y、Z三个 方向的金相照片。（a) X方向的金相照片；（b) Y方向的金相照片；（c) Z方向的金相照片。
[0020] 图4是经过热压缩-等通道转角挤压-预回复-固溶-时效（120°CX48 h)处理后的 实施例二合金的X、Y、Z三个方向的金相照片。（a)X方向的金相照片；（b) Y方向的金相照片； (c) Z方向的金相照片。
[0021] 图5是经过热压缩-预回复-固溶-时效（120°CX48 h)处理后的对比例三合金的X、 Y、Z三个方向的金相照片。（a)X方向的金相照片；（b) Y方向的金相照片；（C) Z方向的金相 照片。
[0022] 图6是经过热压缩-固溶-时效（120°C X 48 h)处理后的对比例四合金的X、Y、Z三个 方向的金相照片。（a) X方向的金相照片；（b) Y方向的金相照片；（c) Z方向的金相照片。
具体实施方式
[0023] 下面结合附图和实施例对本发明作进一步的说明。
[0024] 实施例一。
[0025] 如图1、2、3所示。
[0026] —种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，以实测质量分数为 Al -13.01Zn -3.16Mg -2.8Cu -0.204Zr -0.0757Sr的挤压态超高强铝合金为例，切割取 样后，进行第一次的热压缩，将超高强铝合金加热至400±5°C，保温2±0.5h后进行变形量 为50%的压缩变形(也可大于50%);之后将超高强铝合金加热至400 ± 5°C，保温2 ± 0.5h后再 放入凹模通道夹角Φ=11〇°的模具中进行等通道转角挤压处理以细化热压缩后的铝合金晶 粒;然后将超高强铝合金进行250±5°CX 24±lh、300±5°CX 6 ±lh和400±5°CX 6土 I h的三次预回复退火处理；随后，对预回复后的合金进行450±5°C'2 ±0.5h+460±5°C'2 ±0.5 h+470±5TT2 ±0.5h的强化固溶处理（最佳参数为450ΤΓ2 h+460TT2 h+47(T(T2 h)，固溶结束后立即水淬，水温为25±5°C;水淬处理后，对合金进行120°CX48 h的时效处 理。最后对样品的X、Y方向的硬度，导电率，强度进行测量，对其进行XRD，EBSD分析，进行晶 间腐蚀，剥落腐蚀实验，以得到其峰值时效时各方面的性能指标，并与只进行热压缩-预回 复-强化固溶及时效处理(对比例一）的试样和只进行热压缩-强化固溶及时效处理(对比例 二）的试样对比。
[0027] 实验结果如下(表1和表2): 表1.超高强铝合金X方向（横向）的各个性能指标
表2.超高强铝合金Y方向（纵向）的各个性能指标
实验结果表明，热压缩-等通道转角挤压-预回复前处理及后续的强化时效处理对六1_ 13.01Zn -3.16Mg -2.8Cu -0.204Zr -0.0757Sr合金的硬度几乎没有影响，导电率略有下 降。热压缩-等通道转角挤压-预回复前处理后的合金相比只进行热压缩-预回复-固溶-时 效处理(对比例一)和只进行热压缩-固溶-时效处理(对比例二)其X、Y方向延伸率明显得到 提升，即材料的横向纵向塑性显著提高。虽然强度有所降低，但基本满足了高强度铝合金强 度要求。同时经过热压缩-等通道转角挤压-预回复-固溶-时效处理的合金Χ、Υ方向（横向、 纵向）的屈服强度和极限强度相差无几，表明实施例一的各向同性得到了提高，反而对比例 一和对比例二的Χ、Υ方向屈服强度和极限强度差异大，即各向异性较大。图1中可以看出经 过ECAP加工挤压后X和Z方向的晶体等轴化，无方向性，即各向同性得到提高。因此上述说明 ECAP处理使得合金晶体的各向同性和塑性得到了显著提高。
[0028] 实施例二。
[0029] 如图4、5、6所示。
[0030] —种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，以实测质量分数为 Al -10.78Zn -2.78Mg -2.59Cu -0.22Zr -0.047Sr的挤压态超高强铝合金，切割取样后， 进行第一次的热压缩，将超高强铝合金加热至400±5°C，保温2±0.5h后进行变形量为50% 的压缩变形;之后将超高强铝合金再次加热至400 ± 5°C，保温2 ±0.5h后再放入凹模通道夹 角Φ=110°的模具中进行ECAP挤压处理;然后将超高强铝合金进行250±5°CX 24 h、300 ±5°CX 6 h和400±5°CX 6 h的三次预回复退火处理。随后，对预回复后的合金进行450 °CT2 h+460°CT2 h+470°CT2 h的强化固溶处理，固溶结束后立即水淬，水温为25±5°C。水 淬处理后，对合金进行120 °C X 48 h的时效处理。最后对样品的Y方向的硬度，导电率，强度 进行测量，对其进行XRD，EBSD分析，进行晶间腐蚀，剥落腐蚀实验，以得到其峰值时效时各 方面的性能指标，并与只进行热压缩-预回复-强化固溶及时效处理(对比例三)的试样和只 进行热压缩-强化固溶及时效处理(对比例四）的试样对比。
[0031] 实验结果如下(表3): 表3.超高强铝合金Y方向（纵向）的各个性能指标
实验结果表明，热压缩-ECAP-预回复前处理使六1-10.78211-2.781^-2.59(：11-0.22Zr -0.047Sr合金的硬度略有下降，导电率提高，热压缩-ECAP—预回复前处理后的合 金相比只进行热压缩-预回复-固溶-时效处理(对比例三)和只热压缩-固溶-时效处理(对 比例四）的延伸率明显得到提升，提升了82.8%和88.2%左右，即材料纵向塑性得到明显的大 幅度提升。其晶粒尺寸得到了细化，抗晶间腐蚀能力也有很大提高。
[0032] 实施例三。
[0033] —种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，以实测质量分数为 Al -12Zn -3Mg -2.7Cu -0.21Zr -0.066Sr的挤压态超高强铝合金，切割取样后，进行第一 次的热压缩，将超高强铝合金加热至400 ± 5°C，保温2 ±0.5h后进行变形量为50%的压缩变 形；之后将超高强铝合金再次加热至400 ± 5 °C，保温2 ± 0.5h后再放入凹模通道夹角Φ = 110°的模具中进行ECAP挤压处理;然后将超高强铝合金进行250±5°CX 24 h、300±5°C X 6 h和400±5°CX 6 h的三次预回复退火处理。随后，对预回复后的合金进行450°CT2 h +460°CT2 h+470°CT2 h的强化固溶处理，固溶结束后立即水淬，水温为25 ± 5°C。水淬处理 后，对合金进行120ΓΧ6 h的时效处理。最后对样品的Y方向的硬度，导电率，强度进行测 量，对其进行XRD，EBSD分析，进行晶间腐蚀，剥落腐蚀实验，以得到其峰值时效时各方面的 性能指标，并与只进行热压缩-预回复-强化固溶及时效处理(对比例三）的试样和只进行热 压缩-强化固溶及时效处理(对比例四）的试样对比。实验结果表明，热压缩-ECAP-预回复前 处理使Al -12Zn -3Mg -2.7Cu -0.21Zr -0.066Sr合金的硬度略有下降，导电率提高，热压 缩-ECAP--预回复前处理后的合金相比只进行热压缩-预回复-固溶-时效处理(对比例三） 和只热压缩-固溶-时效处理（对比例四）的延伸率明显得到提升，提升了82.1%和88.0%左 右，即材料纵向塑性得到明显的大幅度提升。其晶粒尺寸得到了细化，抗晶间腐蚀能力也有 很大提尚。
[0034]实施例四。
[0035] 本实施例与实施例三的区别在于时效处理参数为120°CX24 h，其余与实施例三 相同，实测结果与实施例三变化不大。
[0036] 实施例五。
[0037] 本实施例与实施例三的区别在于时效处理参数为100°CX24 h，其余与实施例三 相同，实测结果与实施例三变化不大。
[0038] 实施例六。
[0039] 本实施例与实施例三的区别在于时效处理参数为100°CX6 h，其余与实施例三相 同，实测结果与实施例三变化不大。
[0040] 本发明未涉及部分与现有技术相同或可采用现有技术加以实现。
Claims (7)
1. 一种大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其特征在于它由前处 理和后处理组成，所述的前处理为依次进行的一次热压缩、等通道转角挤压和预回复处理， 所述的后处理为后续强化热处理。
2. 根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的一次热压缩是将超高强铝合金加热至400±5°C，保温2±0.5h后进行变形量 不小于50%的压缩变形。
3. 根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的等通道转角挤压是将经过一次热压缩的超高强铝合金再次加热至400±5°C， 保温2 ± 0.5h后放入模具中进行等通道转角挤压处理。
4. 根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的预回复处理是将经过等通道转角挤压处理的超高强铝合金进行250±5°C X 24±lh、300±5°CX 6±lh和400±5°CX 6±1 h的预回复退火处理。
5. 根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的后续强化热处理为固溶处理+时效处理。
6. 根据权利要求5所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的固溶处理是指对经过预处理的超高强错合金进行450±5°C X 2±0.5h、460土 5 °C X 2 ± 0 · 5h和470 ± 5 °C X 2 ± 0 · 5h的强化固溶处理；所述时效处理是指将经过固溶处理 的超高强铝合金在常温下立即进行水淬，水淬温度为25±5°C，然后进行100°C X 6h〜48 h (梯度为6h)或120°CX6 h〜48 h (梯度为6h)的时效处理。
7. 根据权利要求1所述的大幅提高超高强铝合金横向纵向塑性及各向同性的方法，其 特征是所述的超高强铝合金为经过均质化处理的挤压态7000系(Al-Zn-Mg-Cu)合金，它主 要由铝(Al)、锌(Zn)、镁(Mg)、铜(Cu)、锆(Zr)、锶(Sr)组成，其中锌(Zn)的质量百分比10.78 〜13.01%，镁(Mg)的质量百分比为2.78〜3.16%，铜(Cu)的质量百分比2.59〜2.8%，锆(Zr)的质 量百分比0.204〜0.22%，锶(Sr)的质量百分比0.047〜0.0757%，余量为铝和少量杂质元素，各 组份的质量百分比之和为100%。
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