CN101994032B - Be-Nb-RE高强耐热铝合金材料及其制备方法 - Google Patents
Be-Nb-RE高强耐热铝合金材料及其制备方法 Download PDFInfo
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- CN101994032B CN101994032B CN 200910306152 CN200910306152A CN101994032B CN 101994032 B CN101994032 B CN 101994032B CN 200910306152 CN200910306152 CN 200910306152 CN 200910306152 A CN200910306152 A CN 200910306152A CN 101994032 B CN101994032 B CN 101994032B
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- 239000000956 alloy Substances 0.000 title claims abstract description 178
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 229910000838 Al alloy Inorganic materials 0.000 title abstract description 102
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 152
- REDXJYDRNCIFBQ-UHFFFAOYSA-N aluminium(3+) Chemical class data:image/svg+xml;base64,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 data:image/svg+xml;base64,PD94bWwgdmVyc2lvbj0nMS4wJyBlbmNvZGluZz0naXNvLTg4NTktMSc/Pgo8c3ZnIHZlcnNpb249JzEuMScgYmFzZVByb2ZpbGU9J2Z1bGwnCiAgICAgICAgICAgICAgeG1sbnM9J2h0dHA6Ly93d3cudzMub3JnLzIwMDAvc3ZnJwogICAgICAgICAgICAgICAgICAgICAgeG1sbnM6cmRraXQ9J2h0dHA6Ly93d3cucmRraXQub3JnL3htbCcKICAgICAgICAgICAgICAgICAgICAgIHhtbG5zOnhsaW5rPSdodHRwOi8vd3d3LnczLm9yZy8xOTk5L3hsaW5rJwogICAgICAgICAgICAgICAgICB4bWw6c3BhY2U9J3ByZXNlcnZlJwp3aWR0aD0nODVweCcgaGVpZ2h0PSc4NXB4JyB2aWV3Qm94PScwIDAgODUgODUnPgo8IS0tIEVORCBPRiBIRUFERVIgLS0+CjxyZWN0IHN0eWxlPSdvcGFjaXR5OjEuMDtmaWxsOiNGRkZGRkY7c3Ryb2tlOm5vbmUnIHdpZHRoPSc4NS4wJyBoZWlnaHQ9Jzg1LjAnIHg9JzAuMCcgeT0nMC4wJz4gPC9yZWN0Pgo8dGV4dCB4PSczNS4wJyB5PSc1My42JyBjbGFzcz0nYXRvbS0wJyBzdHlsZT0nZm9udC1zaXplOjIzcHg7Zm9udC1zdHlsZTpub3JtYWw7Zm9udC13ZWlnaHQ6bm9ybWFsO2ZpbGwtb3BhY2l0eToxO3N0cm9rZTpub25lO2ZvbnQtZmFtaWx5OnNhbnMtc2VyaWY7dGV4dC1hbmNob3I6c3RhcnQ7ZmlsbDojM0I0MTQzJyA+QTwvdGV4dD4KPHRleHQgeD0nNTEuMCcgeT0nNTMuNicgY2xhc3M9J2F0b20tMCcgc3R5bGU9J2ZvbnQtc2l6ZToyM3B4O2ZvbnQtc3R5bGU6bm9ybWFsO2ZvbnQtd2VpZ2h0Om5vcm1hbDtmaWxsLW9wYWNpdHk6MTtzdHJva2U6bm9uZTtmb250LWZhbWlseTpzYW5zLXNlcmlmO3RleHQtYW5jaG9yOnN0YXJ0O2ZpbGw6IzNCNDE0MycgPmw8L3RleHQ+Cjx0ZXh0IHg9JzU2LjQnIHk9JzQ0LjMnIGNsYXNzPSdhdG9tLTAnIHN0eWxlPSdmb250LXNpemU6MTVweDtmb250LXN0eWxlOm5vcm1hbDtmb250LXdlaWdodDpub3JtYWw7ZmlsbC1vcGFjaXR5OjE7c3Ryb2tlOm5vbmU7Zm9udC1mYW1pbHk6c2Fucy1zZXJpZjt0ZXh0LWFuY2hvcjpzdGFydDtmaWxsOiMzQjQxNDMnID4zPC90ZXh0Pgo8dGV4dCB4PSc2NC40JyB5PSc0NC4zJyBjbGFzcz0nYXRvbS0wJyBzdHlsZT0nZm9udC1zaXplOjE1cHg7Zm9udC1zdHlsZTpub3JtYWw7Zm9udC13ZWlnaHQ6bm9ybWFsO2ZpbGwtb3BhY2l0eToxO3N0cm9rZTpub25lO2ZvbnQtZmFtaWx5OnNhbnMtc2VyaWY7dGV4dC1hbmNob3I6c3RhcnQ7ZmlsbDojM0I0MTQzJyA+KzwvdGV4dD4KPC9zdmc+Cg== [Al+3] REDXJYDRNCIFBQ-UHFFFAOYSA-N 0.000 claims abstract description 151
- 238000007670 refining Methods 0.000 claims abstract description 57
- 238000005266 casting Methods 0.000 claims abstract description 45
- 238000005275 alloying Methods 0.000 claims abstract description 37
- 229910052802 copper Inorganic materials 0.000 claims abstract description 29
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 26
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 76
- 229910052751 metal Inorganic materials 0.000 claims description 62
- 239000002184 metal Substances 0.000 claims description 62
- 229910052782 aluminium Inorganic materials 0.000 claims description 59
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminum Chemical compound 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[Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 55
- 239000004411 aluminium Substances 0.000 claims description 50
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- 238000003756 stirring Methods 0.000 claims description 30
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- 239000003795 chemical substances by application Substances 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 17
- 239000007788 liquid Substances 0.000 claims description 17
- 239000000155 melt Substances 0.000 claims description 17
- 239000002893 slag Substances 0.000 claims description 17
- 229910052719 titanium Inorganic materials 0.000 claims description 17
- 229910052726 zirconium Inorganic materials 0.000 claims description 17
- 229910052796 boron Inorganic materials 0.000 claims description 14
- 238000007872 degassing Methods 0.000 claims description 14
- 238000003723 Smelting Methods 0.000 claims description 12
- 239000000470 constituent Substances 0.000 claims description 12
- 229910018087 Al-Cd Inorganic materials 0.000 claims description 10
- 229910018131 Al-Mn Inorganic materials 0.000 claims description 10
- 229910018167 Al—Be Inorganic materials 0.000 claims description 10
- 229910018188 Al—Cd Inorganic materials 0.000 claims description 10
- 229910018182 Al—Cu Inorganic materials 0.000 claims description 10
- 229910018461 Al—Mn Inorganic materials 0.000 claims description 10
- 229910018575 Al—Ti Inorganic materials 0.000 claims description 10
- 229910018580 Al—Zr Inorganic materials 0.000 claims description 10
- 238000010309 melting process Methods 0.000 claims description 10
- 229910052793 cadmium Inorganic materials 0.000 claims description 6
- 239000002994 raw material Substances 0.000 claims description 5
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- 239000000654 additive Substances 0.000 description 29
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- 230000000996 additive Effects 0.000 description 28
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- 150000002910 rare earth metals Chemical class 0.000 description 25
- RYGMFSIKBFXOCR-UHFFFAOYSA-N copper Chemical compound 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- 238000002425 crystallisation Methods 0.000 description 21
- 230000005712 crystallization Effects 0.000 description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 21
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- 239000000047 product Substances 0.000 description 17
- 239000011159 matrix material Substances 0.000 description 16
- 239000010936 titanium Substances 0.000 description 16
- 238000000034 method Methods 0.000 description 15
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium(0) Chemical compound 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[Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 13
- 238000005336 cracking Methods 0.000 description 13
- PWHULOQIROXLJO-UHFFFAOYSA-N manganese Chemical compound 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- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium Chemical compound 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- 238000005516 engineering process Methods 0.000 description 12
- 238000002844 melting Methods 0.000 description 11
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N boron Chemical compound 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- VHHHONWQHHHLTI-UHFFFAOYSA-N Hexachloroethane Chemical compound 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ClC(Cl)(Cl)C(Cl)(Cl)Cl VHHHONWQHHHLTI-UHFFFAOYSA-N 0.000 description 9
- 229910052784 alkaline earth metal Inorganic materials 0.000 description 9
- 229910052728 basic metal Inorganic materials 0.000 description 9
- 150000003818 basic metals Chemical class 0.000 description 9
- 150000001638 boron Chemical class 0.000 description 9
- 239000000460 chlorine Substances 0.000 description 9
- 229910052801 chlorine Inorganic materials 0.000 description 9
- ZAMOUSCENKQFHK-UHFFFAOYSA-N chlorine atom Chemical compound 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[Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 9
- 238000004939 coking Methods 0.000 description 9
- 150000001875 compounds Chemical class 0.000 description 9
- 229910052736 halogen Inorganic materials 0.000 description 9
- CNFDGXZLMLFIJV-UHFFFAOYSA-L manganese(II) chloride tetrahydrate Chemical compound 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[Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 238000003913 materials processing Methods 0.000 description 1
- 235000012054 meals Nutrition 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
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- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
- 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 description 1
Abstract
本发明公开了一种高强耐热铝合金材料及其制备方法,按重量百分比计其成分为Cu:1.0~10.0%,Mn:0.05~1.5%,Cd:0.01~0.5%,Ti:0.01~0.5%,B:0.01~0.2%,Zr:0.01~1.0%,Be:0.001~0.1%,Nb:0.01~1.0%,RE:0.05~5%,其余为Al。本发明以优质熔体、固溶体和相图理论为指导,通过优选合金主元素Cu、Mn及RE配方,降低合金准固相温度范围,解决铸造时热裂倾向大、制品高温强度低等问题;优选低成本多元微合金化元素配方,为固溶体中高温相和强化相的培育和细晶化作用创造物质基础条件,最终研制出一种高强耐热铝合金材料。
Description
Be-Nb-RE高强耐热铝合金材料及其制备方法
技术领域
[0001] 本发明涉及一种铝合金材料及其制备方法,特别涉及一种微合金化元素及稀土元素的铝合金材料及其制备方法。
背景技术
[0002] 铝合金是一种较年轻的金属材料,在20世纪初才开始工业应用。第二次世界大战期间,铝材主要用于制造军用飞机。战后,由于军事工业对铝材的需求量骤减,铝工业界便着手开发民用铝合金,使其应用范围由航空工业扩展到建筑业、容器包装业、交通运输业、电力和电子工业、机械制造业和石油化工等国民经济各部门,应用到人们的日常生活当中。现在,铝材的用量之多,范围之广,仅次于钢铁,成为第二大金属材料。
[0003] 从制造业和铝合金制品的角度,习惯上把高强度铝合金分为变形铝合金和铸造铝合金两类;从制品可用的温度条件划分,高强度铝合金又分为普通铝合金和高温(或耐热)铝合金。到目前为止,能够满足高温高强需要的,只有Al-Cu系铝合金,从牌号系列上讲,Al-Cu系合金包括铸造铝合金和变形铝合金,而不论铸造还是变形,都属于2系铝合金;而能够同时满足铸造性能好又容易进行变形加工的高温高强度铝合金,还没有见公开报道过。
[0004] 1、高强度铸造铝合金和变形铝合金
[0005] 一般铸造铝合金包括AlSi系、AlCu系、AlMg系和AlZn系4个系列,其中以AlCu系和AlZn系铝合金的强度最高,但多数在200Mpa〜300Mpa之间,高于400Mpa的只有AlCu系的少数几个牌号,但因采用精铝基体且加入贵重元素,制造成本很高;Α1Ζη系铸造合金的耐热性能很差。因此,一般铸造铝合金与变形铝合金相比因强韧性稍逊使其应用范围受到较大的限制。许多 重要用途如特种重载车负重轮、航空用铝合金等多采用变形铝合金,而不是铸造铝合金。变形铝合金通过挤压、轧制、锻造等手段减少了缺陷,细化了晶粒,提高了致密度,因而具有很高的强度、优良的韧性以及良好的使用性能。但是,对设备和工装模具要求高,工序多,因此变形铝合金生产周期长、成本很高。与变形铝合金相比,铸造铝合金具有价格低廉、组织各向同性、可以获得特殊的组织、易于生产形状复杂的零件、可以小批量生产也可以大批量生产等诸多优点。因此,开发出能够替代部分变形铝合金的高强韧铸造铝合金材料及其铸造成形工艺,可以达到以铸代锻、缩短制造周期、降低制造成本的目的,具有重要的理论意义和重大的实际应用价值。
[0006] 在高强韧铸造铝合金的发展过程中,法国于20世纪初研制成功的A-U5GT占有重要的地位,在目前具有代表性的高强韧铸造铝合金中它的历史最久、应用最为广泛。我国目前没有与它对应的牌号。
[0007] 美国铝协会牌号201.0(1986年)和206.0(1967年)后是在A-U5GT基础上改造而形成的,具有很好的力学性能和抗应力腐蚀能力。但由于含有0.4%〜1.0%的银,材料成本很高,仅用于军事或其他要求高的领域,限制了其应用范围。
[0008] 在高强韧铸造铝合金领域,我国取得了世界瞩目的成绩。60年代至70年代,北京航空材料研究院研制成功了 ZL205A合金。ZL205A合金成分复杂,含有Cu,Mn,Zr,V,Cd,Ti,B等7种合金元素。ZL205A(T6)的抗拉强度为5lOMPa,是目前已有注册牌号的铸造铝合金材料强度最高的。ZL205A(T5)的强韧性最好,延伸率可达13%。但ZL205A最大的缺陷是铸造性能差、热裂倾向性大,同时因配方成本高,应用范围小。
[0009] 上述3种高强韧铸造铝合金同属于Al-Cu系。该系列合金强度高,塑性和韧性也较好。但铸造性能较差,具体表现为热裂倾向大、流动性较差、补缩困难。此外,该系列合金抗蚀性能较差,有晶间腐蚀倾向。该系列合金的铸造成品率很低。
[0010]此外,已经公开的申请号为 200810302670.3,200810302668.6,200810302669.0和200810302671.8的4个专利名称均为“一种高强度铸造铝合金材料”的文献中介绍了一种由Cu、Mn、T1、Cr、Cd、Zr、B和稀土元素组成的高强度铸造铝合金材料,这种铝合金材料具有较高的抗拉强度和延伸率,抗拉强度达到了 440Mpa,延伸率大于6% ;但此类高强度铸造铝合金材料在使用过程中仍未能解决热裂倾向大的问题、合金强度与可铸性的矛盾突出,其主要原因是在合金主元素Cu 、Mn成分范围,合金准固相温度范围较宽,铸造凝固时为具有各向异性的枝晶发育提供了充分条件,在凝固后期形成强大的内部收缩应力,故而收缩热裂倾向大。
[0011]目前正式注册的2XXX系变形铝合金牌号有70多个,绝大多数是美国注册的,其中只有 2001、2004、2011、2011A、2111、2219、2319、2419、2519、2021、2A16、2A17、2A20、2B16 等14个牌号是铜含量在5%以上的高铜铝合金,而其中铜含量在6%以上的只有2A16、2A17、2A20、2B16这4个牌号。这些变形铝合金配方中都含有较多的S1、Mg、Zn等成分,而没有稀土(RE)等起微合金化作用的元素,因此其配方组成与2系铸造铝合金相差甚远,反映出两种属性的铝合金不同的生产工艺和深加工工艺。
[0012] 2、高温铝合金
[0013] 高温合金又称耐热高强合金、热强合金或超合金,是在20世纪40年代随着航空涡轮发动机的出现发展起来的一种重要金属材料,能在高温氧化气氛和燃气腐蚀条件下长期承受较大的工作负荷,主要用于燃气轮机的热端部件,是航空航天、舰船、发电、石油化工和交通运输工业的重要结构材料。其中有些合金亦可用于生物工程作骨科和齿科材料。
[0014] 常用的高温合金包括镍基、铁基和钴基合金,能在600〜1100°C高温环境下工作;而耐热铝合金则是冷战期间发展起来的。耐热高强铝合金适于在400°C以下的热环境中长期承受较大的工作载荷,在航空航天、重工机械等领域得到越来越多的应用。除航空涡轮发动机、燃气轮机等直接与高温燃气接触的部件之外,其余高温高压强动力部件均可采用耐热闻强招合金铸造。
[0015] 由于铝合金比较容易加工,随着加工技术水平的提高,在强度满足要求的情况下,人们越来越多地采用变形铝合金替代铸造铝合金。因此耐热高强铝合金又分为铸造用合金和变形用合金两大类。
[0016] 一般说来,耐热高强合金都含有多种合金化元素,多的达十余种。所加入的元素在合金中分别起固溶强化、弥散强化、晶界强化和表面稳定化等作用,使合金能在高温下保持高的力学性能和环境性能。
[0017] 选用铸造用高温合金时应考虑的因素:
[0018] (I)铸件的正常工作温度、最高和最低的工作温度以及温度变化的频率。[0019] (2)铸件本身的温差范围及合金的膨胀性能。
[0020] (3)铸件承受的载荷性能,加载、支承和外部约束方式。
[0021] (4)对铸件的寿命要求和容许的变形量、工作环境和性质、成形方法和成本因素等。[0022] 目前用于高温零部件铸造的铝合金材料,国家标准中只有A201.0、ZL206、ZL207、ZL208、206.0几种牌号,包括铝铜锰系合金及铝稀土系合金;其中,铝铜锰系合金多数以高纯级铝锭为合金材料,成本较高,而铝稀土系合金则在室温下力学性能相对较差。而且,目前耐热高强铝合金普遍存在着高温强度低(250°C以上瞬时抗拉强度小于200Mpa,持久强度小于IOOMpa)、配方成本高、铸造性能差、铸件合格率低、废品料及渣料回用性差等缺陷,造成铸件质量差、成本高、渣料处理流程长等问题。此外,近年来申报的多数耐热铝合金专利新配方中也都含有贵重元素,而且铸造性能差,质量无法满足航空技术进步的要求,不适于产业化生产应用。
[0023] 而在国民经济和国防现代化建设和发展中具有广泛用途和极光明前景的耐热高强变形铝合金,国内外文献中报导较少,已知的2219、2A02、2A04、2A06、2A10、2A11、2A12、2A14、2A16、2A17、2A50、2A70、2A80等2XXX系变形铝合金及7A04等7XXX系变形铝合金,在250°C以上温度下强度多数小于lOOMpa,而其主要合金元素除Cu、Mn外,都是以S1、Mg、Zn作为主微合金化元素,而不添加这几种元素、且250°C以上温度下强度在150Mpa以上的耐热高强变形铝合金材料未见报导。
[0024] 综上所述,可知目前国内外在耐热高强度铝合金领域研究中存在的问题有:高温强度和耐久性不足,250°C以上高温瞬时强度均小于250Mpa,高温持久强度均小于IOOMpa ;材料加工性能差;废料处理流程长、成本高,无法满足航空技术进步的要求等。
发明内容
[0025] 本发明所要解决的技术问题是,针对目前高强度铝合金领域存在的熔体处理工艺粗放、质量差、热裂倾向大、铸造性能差,制品成品率低、高温强度低、废品料及渣料回用性差等技术难题,以优质熔体、固溶体和相图理论为指导,通过优选合金主元素Cu、Mn及稀土元素配方,降低合金准固相温度范围,解决铸造时热裂倾向大、制品高温强度低(包括瞬时强度和持久强度)的带有普遍性的问题;优选低成本多元微合金化元素配方,为固溶体中高温相和强化相的培育和细晶化作用创造物质基础条件;以及优化熔炼、热处理工艺技术,实现固溶体中高温相和强化相的足量培育和细晶化作用的充分发挥。最终研制出一种稀土多元微合金化的AlCu系新型高强耐热(铸造性和变形性)铝合金材料。
[0026] 本发明的技术方案是,按重量百分比计,该合金成分为Cu:1.0〜10.0%,Mn:
0.05 〜1.5%,Cd:0.01 〜0.5%,T1:0.01 〜0.5%,B:0.01 〜0.2%,Zr:0.01 〜1.0%,Be:0.001 〜0.1%, Nb:0.01 〜1.0%,稀土元素 RE:0.05 〜5%,其余为 Al。
[0027] 上述的稀土元素RE为单一稀土元素或一种以上的混合稀土元素。
[0028] 上述的稀土元素RE包括La、Ce、Pr、Nd、Er和Y。
[0029] 该新型高强耐热铝合金的制备方法包括如下步骤:
[0030] (I)在上述元素比例范围内,选定一组可行的元素比例,再根据需要配制的合金总量,推算出所需的每种单质金属的质量,或者中间合金的质量,或者混合金属添加剂(包括盐类化合物)的质量,编制合金生产配料表,并按配料表选足备料。
[0031] (2)往熔炼炉中加入适量的铝锭或熔融铝液,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0032] (3)再按配方比例先加入 Mn、T1、Zr、Be、Nb 纯金属或 Al-Mn、Al-T1、Al-Zr、Al_Be、Al-Nb中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu、Cd纯金属或Al-Cu、Al-Cd中间合金或者混合金属添加剂(包括盐类化合物),再加入B和稀土元素RE,搅拌均匀。
[0033] 其中,混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品。粉末冶金制品包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成;熔剂是指碱金属或碱土金属齒素盐类的混合物(如NaCl、KCl、Na3AlF6等)
[0034] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0035] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0036] (6)铸造(在铸模中结晶凝固)。
[0037] (7)为了防止材料过烧,确定对铸件进行470〜560°C、30小时以内的固溶处理。
[0038] 与现有技术相比,本发明具有如下主要优点:
[0039] 解决了目前Al-Cu系高强韧铝合金(ZL201A、ZL 204A、ZL 205A等)大多采用精铝为基体原料并加入千分之一·以上贵重元素,成本较高,导致Al-Cu系高强韧铝合金只能用于航空航天、国防军工等尖端领域,民用领域因性价比不高而应用受限的问题。
[0040] 随着中国和世界铝产量的快速增长和铝产业规模在中国的不断扩大,“以铝代钢”日渐成为产业发展的趋势和潮流,而在民用领域也迫切需要性价比高的高强韧铝合金;本发明通过采用普铝为基体原料,不加(或少加)贵重元素,优选特征微合金化元素配方,以及采用集约、简练的熔铸、净化等工艺,研制出新型高强耐热铝合金材料,克服了现有材料的在成本上的门槛。
[0041] 具体说来,本发明具有以下八个优点。
[0042] 1、高强度和高硬度。从材料强度看,在满足塑性要求前提下,可通过热处理等工艺技术手段,使各种强化相在铸态组织中充分、均匀、合理析出和分布,使材料强度达到480 〜540MPa ;硬度彡 HB140。
[0043] 2、材料的双重属性。从材料用途属性上看,它属于两性铝合金,既有铸造铝合金的特性又有变形铝合金的特性,既可以直接用于铸造各类轻强功能件和结构件,也可以先铸成棒材再进行热挤压成为各种断面的型材。
[0044] 本质上,该材料属于多元微合金化的铸造铝合金,但由于材料具有极好的流动性及晶间自润滑性能,使其同时具备了变形铝合金的易加工特性。
[0045] 3、工艺的先进性。从生产工艺上看,在熔炼技术上改变了传统的粗放工艺,可使用电炉进行严密的保护性熔炼,从而避免了熔体混入过多的杂质和气体,既保持了合金的纯净度,也简化和缩短了复杂的后续熔体处理流程;同时,熔炼过程较传统反射式熔炼工艺大大提高了能源利用率并降低了对环境的污染,属于绿色环保节能型工艺。[0046] (I)保护性熔炼显著降低了能耗、污染,简化了生产流程,提高了集约化程度
[0047] 由于铝及铝合金熔体具有极强的吸气倾向,故在敞开式或封闭性不好的炉内融化和熔炼时,熔融的合金液会大量地吸收空气中的O2、水分等气体,生成不溶性的Al2O3和具有良好活性的H2,在熔体中形成杂质和气体,如果不及时除去,会在铸造时形成铸件的夹渣、气孔、疏松等缺陷,导致制品报废;其中尤其以熔体中H2的危害最大,因为H2在铝及铝合金熔融态时的溶解度大大高于固态时的溶解度,因此在凝固时,会有大量的H2从合金中逸出造成大量缺陷。而不溶性渣则相对较易除去。因此,避免熔体吸气是保持熔体质量和铸造质量的重要措施。
[0048] 普通的大型工业铝合金熔炼炉是以液体或气体燃料为能源的反射式加热炉或保温炉,需要大量的空气助燃,同时燃烧产物中含有大量水蒸汽和C02、NOx等物质,在高温下极易与铝发生化学反应而生成各种有害杂质,同时这些杂质本身与铝液一样极易吸附H2,使熔体受到严重污染,在进行铸造之前,熔体必须经历一道或几道专门的净化工序,并经取样检测合格后方可进入铸造流程,这无疑延长了作业流程,能耗和污染指标都难以降低;同时因为生产的连续性要求,必须使装备大型化,增加了投资,提高了技术准入门槛;而设备的大修成本、启动成本均随着设备的大型化和长流程而成倍增长。
[0049] 而一般的铝合金铸造件生产车间,由于产量规模小,设备简单粗放,对铝合金熔体很少采取密闭保护措施,同样造成熔体质量和铸造质量不高。
[0050] 本发明要求的制备方法,其熔炼方式是采用带密封盖的感应电热设备,根除了燃料燃烧时空气、水蒸汽和各种燃烧产物对熔体的污染,同时在熔炼过程中,可采用保护性气体进行保护气氛熔炼,最大程度地隔绝空气的侵袭;由于保持了熔体的高纯洁性,在其后的铸造阶段可采取很简单的通过式除气、除渣装置,而不必添加专门的停留式保温净化设备,从而大大简化了工艺流程。
[0051] (2)优化了铸件的热处理工艺,避免了因“过烧”而造成的材料力学性能降低、制品报废的发生
[0052] 申请号为 20081030267`0.3,200810302668.6,200810302669.0 和 200810302671.8
的4个专利名称均为“一种高强度铸造铝合金材料”的发明中,规定材料的热处理工艺参数为“620°C以下、72小时以内”,在材料应用试验中,发现固溶处理时温度超560 V时,常常会发生“过烧”现象,造成材料微观结构的破坏,其典型特征是强度和延展性等主要指标显著降低,铸件变脆,表面发黑发暗,甚至在热处理过程中即产生裂纹、变形而报废。而当固溶温度低于470°C时,由于强化相的培育、析出强化作用不充分,材料的强度难以达到期望的目标值;同时,在经过多次试验摸索后,发现热处理时间超过30小时,对材料性能的提高没有显著效果。因此,为了提高效果和效率,将热处理工艺参数优化调整为:470〜560°C、30小时以内的固溶处理。
[0053] 4、配方的科学性和经济性。从原料来源上看,先进的配方创造了两方面的优势基体材料优势和合金元素优势。一方面,新材料系列的基体合金可以采用普通工业纯铝(即双零铝,包括铝液和重熔用铝锭),比已有的高强度铝合金必须采用精铝或高纯级铝为基体合金的配方模式,具有原料供应充足、成本低、采购方便等优势;同时,该材料同样可以采用精铝或高纯级铝作为基体合金,而这种配方的材料比该品种的普铝基材料具有更高的延展性。另一方面,因贵重元素对合金成本升高的贡献率是普通元素的数十乃至百倍以上,新材料系列的合金元素组合中多数不采用贵重元素,即使采用,比例也很小,均在千分之一以下;而已有的高强度铝合金贵重元素的比例均在千分之一以上,两方面的优势为系列新材料拓展市场储备了巨大潜力。
[0054] 本发明通过优选合金主元素铜(Cu)、锰(Mn)和以铍(Be)、铌(Nb)为特征微合金化元素的多元配方,为固溶体中高温相和强化相的培育和细晶化作用创造物质基础条件,合金在主元素Cu、Mn形成强化Θ相(Al2Cu)、T相(Al12Mn2Cu)的基础上,选用高温元素铍(Be)、铌(Nb)和稀土元素RE作为复杂合金化的微量添加元素,Be在合金中形成α、β弥散性高温强化相,可防止合金元素的氧化、烧损、吸气,提高合金的冶金质量及表面氧化膜的致密度,可使杂质铁(Fe)由针状变为团粒状,还可防止浇注时砂型铸件与模型的反冲;Nb在合金中形成AlNb3、AlNb、Al3Nb等3种金属化合物弥散性高温强化相;稀土元素RE在铝合金中能形成多种金属化合物(如铝镧有a _AlnLa3、β _AlnLa3、AlLa3等,铝铈有a -Ce3Al11,CeAl3XeAl2 等,铝镨有 a -Al11Pr3' P -AlPr3 等,铝钕有 a -AlnNd3、AlNd3 等,铝钷有 AlnPm3、AlPm2等,铝钐有AlnSm3、AlSm2等,铝铕有Al4Eu、AlEu等,铝钆有Al4GcU Al17Gd2等,铝铽有Al3Tb' AlTb2 等,铝镝有 a -Al3Dy, AlDy2 等,铝钦有 Al3Ho' AlHo2 等,铝铒有 Al-Er =Al3Er,AlEr2等,铝铥有Al3Tnu AlTm等,铝镱有Al3Yb' Al2Yb等,铝镥有Al3Lu' AlLu 2等,铝钇有A13Y、AlY2等,铝钪有Al3Sc、AlSc2等,共有近百种难熔活性金属化合物),都显著提高了合金的室温强度、耐热强度和熔体流动性。
[0055] 本发明的主合金元素作用机理如下。
[0056] ①该材料允许铜(Cu)含量在I〜10%范围,较Al-Cu系铸造铝合金含铜(Cu)量为3〜11%的范围略有不同,但在理论上则具有极为重大的创新意义。
[0057] 一方面,在铜(Cu)含量为5.65〜5.7%时,正好等于Cu在Al-Cu合金中的共晶溶解度,在热处理过程中按照“完全固溶-均匀析出-晶界强化相-晶隙填充剂(粘结、镶嵌、防滑)”的转变模式和作用机理变化,形成较多的富Cu强化相(其中包括Al2Cu即Θ相),从而使铝合金的室温和高温力学性能都大大提高,也改善了加工性能;但由于Cu在Al中的溶解度随温度降低而急剧下降,在结晶凝固过程中,Cu在α-ΑΙ固溶体中的过饱和度快速提高,α -Al枝晶一边长大,一边强烈增加地向晶界外排出富Cu强化相的倾向,造成晶内和晶界间巨大的结构应力,同时合金整体正处于凝固收缩阶段,收缩应力与结构应力叠加在一起,当超过合金的即时实际强度,则形成热裂纹,因此在铜(Cu)含量彡5.65%的一定范围内,铝合金的铸造性能最差、热裂倾向性最大。但总的趋势是,随着铜含量的降低,合金的热裂倾向性也降低;当&1含量< 1%时,其强化相不足,强化相的转变模式和作用机理难以充分发挥,在温度变化时在晶界的析出和向晶内的溶入会形成晶界间较多的缺陷,降低合金的室温和高温强度,所以Cu含量过低,对简单的Al-Cu合金来说没有意义;但如果合金中加入了较多的稀土元素(RE),则可以起到弥补Cu含量过低的特殊效果。
[0058] 另一方面,在Cu含量彡5.7%时,富Cu相在热处理时不能被基体全部吸收,则以边界富Cu金属化合物形态弥散分布于晶界,降低了 α-ΑΙ固溶体内外Cu质点的浓度差,在凝固过程中平缓了 α-Al固溶体枝晶向晶界排出富Cu相的强度,即降低了结构应力和热裂倾向。显然,当Cu含量> 5.7%,富Cu相越多,结晶时合金内部的结构应力和热裂倾向越小;同时,高熔点细晶弥散的富Cu相在熔体结晶时形成活性异质晶核,加速熔体结晶反应但又阻止晶核长大 ,细化了晶粒,也降低了合金热裂倾向性;并使基体晶界之间充填更加饱满;富Cu相还能与Al、Mn等多种元素形成难熔金属化合物。所有这些作用,明显地弱化了熔体的表面张力,降低了熔体粘度,从而显著提高了熔体流动性及合金的铸造性能。
[0059] 当Cu含量处于5.7%左右时,经热处理后,在基体晶界有较多的富Cu相(溶入-析出相)与较少的(约0.5% )Cu基金属化合物细晶弥散相,使室温状态下的合金强度保持较高水平,但当处于高温环境时,因大量富Cu相重新溶入基体中,就会造成较多的晶间空隙和缺陷,这会使合金的高温强度显著下降。随着Cu含量继续增加,合金强度受温度影响的程度减小,而当弥散相与析出相基本处于等量状态时,材料强度受温度变化的影响最低,此时合金中Cu含量应为11〜12 %。
[0060] 但当合金中Cu含量> 10%时,因结晶时过剩的Cu相具有优先结晶性质而形成巨大的网络结构,合金粘度大大增强,过剩相在结晶过程中取代铝基体成为控制结晶的主要因素,原有弥散相 对铝基体相的优良作用全部受到屏蔽,因此合金的各种性能又大幅下降。
[0061] 根据以上理论基础及实践的验证,确定主合金元素Cu含量的合理范围为:1〜10% (wt% )。
[0062] ②该材料以猛(Mn)元素改善抗蚀性,同时屏蔽杂质Fe,减少Fe的有害作用。
[0063] 因锰(Mn)元素与基体作用生成的MnAl6与纯铝具有相同的电位,可以有效地改善合金的抗蚀性和焊接性;同时Mn作为高温强化相,具有提高再结晶温度、抑制再结晶晶粒粗化的作用,能够实现对合金的固溶强化、补充强化、提高耐热性能;在晶粒细化剂作用下,能与Fe元素生成球团状的Al3 (Fe、Mn),有效消除了 Fe对合金的有害作用,因此本发明可允许Fe含量在较宽的范围(Fe ^0.5% ),这样带来的好处是:实现普铝代替精铝,降低成本,扩大原料来源及材料应用领域。
[0064] ③主要使用稀土 RE作为基础微合金化元素,且其含量范围大,最高可达5%,可充分发挥稀土元素在合金中的除气、除渣、净化作用、细化晶粒和变质作用、提高合金的力学性能以及耐蚀性作用。
[0065] 稀土元素除气、除渣、净化作用的机理是:稀土元素在活性很强,对氧、氢、硫、氮等具有较强的亲和力,其脱氧能力超过现有最强的脱氧剂铝,可把含量为50X10_6氧,脱至10 X 10_6以下,其脱硫作用可把含S量为20 X 10_6脱至I〜5 X 10_6。因此,含稀土的铝合金在熔炼时很容易和铝液中的上述物质发生化学反应,反应产物不溶于铝而进入渣中,从而使合金中的气体含量降低,使合金产品产生气孔和缩松的倾向大大降低。
[0066] 稀土元素能显著提高合金的力学性能。稀土元素在铝合金中可形成稳定的高熔点金属间化合物如A14RE、Al8CuRE, Al8Mn4RE, Al24RE3Mn等。这些高熔点金属间化合物弥散分布于呈网状或骨架状的晶间和枝晶间,并与基体牢固结合,起到了强化和稳定晶界的作用。同时,合金中还形成一定数量的AlSiRE相,由于其熔点和硬度很高,因此对提高合金的耐热性和耐磨性均有良好的作用。此外,还可中和金属液中的低熔点杂质元素Sn、Pb、Sb等,与它们形成高熔点的化合物或使他们从枝晶间向整个晶体内均匀分布,消除了枝晶组织。
[0067] 稀土元素有细化晶粒和变质作用。稀土元素为表面活性元素,可集中分布在晶界面上,降低熔体粘度,增强流动性,降低相与相之间的拉力,因为使形成临界尺寸晶核的功减少,结晶核数量增加,从而使晶粒细化。稀土对铝合金的变质作用具有长效性和重熔稳定性,大多数单一或混合稀土加入后对α -Al相有很强的细化和变质作用。
[0068] 此外,稀土元素还能够提高合金的导电性。由于稀土能细化铝晶粒,也能在合金中Fe、Si等杂质形成稳定的化合物(如CeFe5、CeS1、CeSi2等)并从晶内析出,再加上稀土对合金的净化作用,使得铝的电阻率得到降低,导电性提高(约2% )。
[0069] 很少量的稀土元素RE即可对合金性能产生明显的变质改良作用,因此,一般铝合金的稀土加入量在 I % 以下,在 200810302670.3,200810302668.6,200810302669.0 和200810302671.8专利申请中,稀土含量确定为0.05〜0.3%。从Al-RE合金相图分析,由于大部分稀土在铝中的溶解度很小(如Ce约为0.01% ),其存在形态多以高熔点金属间化合物分布于晶界或基晶内部。由于活性很高,在熔体净化中充当净化剂消耗掉一部分,若加入量太少,则其对α-Al相的变质作用就难以充分发挥。为保持稀土变质作用的长效性和重熔稳定性,并充分发挥其高温强化特性,本发明特把铜含量与稀土含量一起考虑,确定其含量范围为0.05〜5%。
[0070] ④铍(Be)元素作为复杂合金化的特征添加元素,在合金中能形成α、β弥散性高温强化相,可防止合金元素的氧化、烧损、吸气,提高合金的冶金质量及表面氧化膜的致密度,可使杂质铁(Fe)由针状变为团粒状,还可防止浇注时砂型铸件与模型的反冲;铌(Nb)元素作为复杂合金化的特征添加元素,在熔体中能够形成AlNb3、AlNb、Al3Nb等3种金属化合物高温强化相;呈弥散相分布于基体晶界,提高合金的室温和高温强度。
[0071] 5、优异的铸造性能。通过在高科技结构、航空、航天、民用重工等几个领域使用的铸件多次铸造试验,验证了该新材料的优异性能:铸造性能高于目前的A201.0、ZL206、ZL207、ZL208、206.0等高强度铸造铝合金,解决了上述铝合金铸造时热裂倾向性大、铸件合格率低的重大问题;旧料回炉重熔与新料可实现任意比例配料,新旧料混合熔体浇注性能无改变,且有稳定材料强度、提高延展性的良好作用,较原有高强度铝合金废料回用性差、循环路线长的状况,具有极显著的经济性和集约性。
[0072] 新材料消除热裂倾向的原理在于:因合金中铜含量增多形成富Cu相,富Cu相作为高熔点细晶弥散相以金属化合物形态弥散分布于晶界,在熔体结晶时有效抵消了晶粒内富Cu溶质因过饱和度急剧升高而形成的向晶界扩散的强烈倾向,从而减缓了结晶时的结构应力;同时晶界上富Cu弥散相 与Be、Nb特征微合金化元素、RE稀土微合金化元素及Mn、Zr、T1、B等元素的多种弥散相,都具有细化晶粒、充填基体晶界、形成近铝电位金属化合物的多种作用,所有这些作用明显地弱化了熔体的表面张力,降低了熔体粘度,从而显著提高了熔体流动性及合金的铸造性能,保证了铸造产品具有较高的合格率。
[0073] 旧料回用性好的原理在于:本发明中多元微合金化作用具有长效性和重熔稳定性,重熔时,熔体的结构特性保持了一次合金熔体形成的原子集团结构和细晶结构,大量的活性晶核能够在熔体中充分发挥凝聚、同化微晶结构的作用,并能保持原有的流动性。因此,旧料的配入有稳定材料强度、提高延展性的良好作用。
[0074] 旧料的这种特性,完全可以实现在生产现场的即时回用,无论是渣料、加工余料还是不合格铸件,均可与新料一同熔炼或直接加入熔体中。
[0075] 本发明的此种特性,较目前大量应用的IXXX系和2XXX系高强度铝合金材料铸造成品率显著提高,大大降低了废品量,因此在生产现场不需要大的废品堆场(实际生产中,铝合金铸造车间往往要规划出很大的废品堆放场地);同时,很多铸造铝合金不具备重熔稳定性,无法在现场直接回用,因此需要组批进行集中处理,占据很大的制造成本,衍生出一系列处理环节和无效劳动;而应用本发明提供的新材料,所有这些额外的环节、成本和无效劳动均可省去。
[0076] 6、优异的加工、表面防腐处理性能。通过将新材料加工成轴、球、管、角材、螺栓等各种形状的成品件的试验,证明材料具有极好的可加工性能,表面可达到近镜面程度的精洁度,光反射率高于纯铝;表面氧化和涂覆试验表明,表面阳极氧化后膜厚可达到标准要求等级、表面颜色无改变,涂料与氧化表面的附着性完全达到抗破坏性试验的标准等级。
[0077] 7、优异的高温性能。该材料具有高温铝合金的特性,可以达到400°C条件下强度高于200Mpa以上,高于传统的高温(耐热)铝合金材料,这一特性使新材料可以替代除航空发动机匣体直接承受高温燃气灼烧的部件之外的其它各部位耐热部件材料。(耐热性原理参见特性4 “配方的科学性和经济性”中关于富铜相、稀土 RE、耐热合金元素Be、Nb等的内容)。
[0078] 8、典型的原创性。该系列新型材料是申请人在取得合金化理论创新突破后快速研发出来的,材料优异性质的验证同时就是对新合金化理论的验证,而这种理论突破目前在所有的文献资料上都没有明确记载过,因此该系列新材料在国际上属于原始性、基础性的重大创新。
[0079] 本发明的创新点
[0080] 表一列出了与本发明在某一方面的性能和用途上相近的31种铝合金的元素组成。可以看出,与已有各种高铜含量变形铝合金、耐热变形铝合金、耐热铸造铝合金相比,本发明主要有以下创新内容。
[0081] 一是铜(Cu)含量允许范围大,在I〜10% ;同时以锰(Mn)元素配合形成多种高温强化相。
[0082] 二是主要使用稀土 RE作为基础微合金化元素,且其含量范围大,最高可达5%,可充分发挥稀土 RE在合金中的除气、除渣、净化作用、细化晶粒和变质作用、提高合金的力学性能以及耐蚀性作用;稀土元素RE对氧、硫、氮、氢的亲和力都很强,因而其脱氧、脱硫、去除氢气和氮气的作用都很强,此外,RE为表面活性元素,可集中分布在晶界面上,降低相与相之间的拉力,因为使形成临界尺寸晶核的功减少,结晶核数量增加,从而使晶粒细化。
[0083] 三是对铁元素的限制比较宽松,允许其含量最大可达0.5%,这为使用普铝为基体进行合金材熔铸开拓了空间。
[0084] 四是不使用镁、锌等低熔点元素作为产生强化相的物质,避免了高温下材料强化相的分解和转化,从而显著提高了材料的高温强度。
[0085] 五是以铍(Be)元素作为复杂合金化的特征添加元素,在合金中能形成α、β弥散性高温强化相,可防止合金元素的氧化、烧损、吸气,提高合金的冶金质量及表面氧化膜的致密度,可使杂质铁(Fe)由针状变为团粒状,还可防止浇注时砂型铸件与模型的反冲;铌(Nb)元素作为复杂合金化的特征添加元素,在熔体中能够形成AlNb3、AlNb、Al3Nb等3种金属化合物高温强化相,呈弥散相分布于基体晶界,提高合金的室温和高温强度。结合使用钛(Ti)、硼(B)、锆(Zr)元素作为综合晶粒细化剂,使合金材料具备了高强高韧耐热和熔体高流动性等全部优良性能的物质基础。
[0086] 以上是本发明特征配方中最明显的五个方面。
[0087] 表一与本发明有关的各 种铝合金化学成分[0088]
[0090]
[0091] 力学性能比较
[0092] 申请人将本发明与现有几种高强韧铝合金的力学性能进行对比,见表二。
[0093] 表二本发明与几种高强韧铸造铝合金的力学性能
[0094 ]
[0095] ①所列数据是高纯的206.0合金,即W(Si)≤0.05%,W(Fe)≤(λ 10%。S-砂型铸造,J-金属型铸造,R-熔模铸造
[0096] 从表二可以看出,本发明的抗拉强度480〜540MPa,硬度大于HB140,明显优于现有高强韧铝合金的力学性能。
[0097] 高温性能
[0098] 申请人对本发明在各种温度条件下的强度高温持久性能进行了测试,并与现有常用耐热铝合金的高温持久性能进行了对比,见表三。
[0099] 表三本发明与常用耐热铝合金的高温持久性能
[0101] 从表三可以看出,本发明的室温强度大于450Mpa,高温强度250°C时在300Mpa以上,高温强度300°C时,高温持久性能大于200Mpa,明显优于已有耐热高强合金的高温持久性。
[0102] 综上所述,本发明Be-Nb-RE高强耐热铝合金材料具有高科技含量、广袤的应用领域和极佳的市场前景,其极优的性价比使其可以替代目前几乎所有高强度铝合金和高温铝合金,代表了中国乃至世界轻强结构材料的发展方向。
具体实施方式
[0103] 实施例1:Cu_l.0特征微合金化兀素-Be、Nb,基础微合金化稀土兀素-镧La
[0104] (I)按配料计算表称量好所需的各种合金元素,如下。
[0106] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0107] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al-Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素La,搅拌均匀。
[0108] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0109] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0110] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0111] (6)铸造(在铸模中结晶凝固)。
[0112] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0113] (8)试样指标:抗拉强度485Mpa,延伸率7.5%。
[0114] 实施例2:Cu-4.2%,特征微合金化兀素-Be、Nb,基础微合金化稀土兀素La、Ce混合稀土
[0115] (I)按配料计算表称量好所需的各种合金元素,如下。
[0116]
[0117] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0118] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al-Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素La、Ce混合稀土,搅拌均匀。
[0119] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0120] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0121] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0122] (6)铸造(在铸模中结晶凝固)。
[0123] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0124] (8)试样指标:抗拉强度538Mpa,延伸率6.7%。
[0125] 实施例3:Cu-5.1 %,特征微合金化元素-Be、Nb,基础微合金化稀土元素Eu
[0126] (I)按下列配料计算表称量好所需的各种合金元素,如下。
[0127]
[0128] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0129] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al_Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素Eu,搅拌均匀。
[0130] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615[0131] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0132] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0133] (6)铸造(在铸模中结晶凝固)。
[0134] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0135] (8)试样指标:抗拉强度503Mpa,延伸率5.1%。
[0136] 实施例4:Cu_6.01 %,特征微 合金化兀素_Be、Nb,基础微合金化稀土兀素_La、Ce、Pr混合稀土
[0137] (I)按配料计算表称量好所需的各种合金元素,如下。
[0139] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0140] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al-Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素La、Ce、Pr混合稀土,搅拌均匀。
[0141] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0142] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0143] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0144] (6)铸造(在铸模中结晶凝固)。
[0145] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0146] (8)试样指标:抗拉强度533Mpa,延伸率4.1%
[0147] 实施例5:Cu-6.5%,特征微合金化元素-Be、Nb,基础微合金化稀土元素铒Er
[0148] (I)按配料计算表称量好所需的各种合金元素,如下。
[0150] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0151] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al-Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素Er,搅拌均匀。
[0152] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0153] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0154] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0155] (6)铸造(在铸模中结晶凝固)。
[0156] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0157] (8)试样指标:抗拉强度527Mpa,延伸率6.9%。
[0158] 实施例6:Cu-7%,特征微合金化兀素-Be、Nb,基础微合金化稀土兀素钕Nd
[0159] (1)按配料计算表称量好所需的各种合金元素,如下。
[0160]
[0161] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0162] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al_Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素Nd,搅拌均匀。
[0163] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0164] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0165] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0166] (6)铸造(在铸模中结晶凝固)。
[0167] (7)对铸件进行470〜560°C、30小时以内的固溶处理。
[0168] (8)试样指标:抗拉强度517Mpa,延伸率5.3%。
[0169] 实施例7:Cu_8%,特征微合金化元素-Be、Nb,基础微合金化稀土元素铺Ce
[0170] (1)按配料计算表称量好所需的各种合金元素,如下。
[0171]
[0172] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0173] (3)再按配方比例先加入Al-Mn、Al-T1、Al-Be、Al-Nb、Al_Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素Ce,搅拌均匀。
[0174] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0175] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0176] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0177] (6)铸造(在铸模中结晶凝固)。
[0178] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0179] (8)试样指标:抗拉强度501Mpa,延伸率4.8%。
[0180] 实施例8:Cu-10%,特征微合金化元素-Be、Nb,基础微合金化稀土元素乾Y
[0181] (I)按配料计算表称量好所需的各种合金元素,如下。
[0182]
[0183] (2)往熔炼炉中加入适量的铝锭,加热使之完全融化并在700〜800°C下保温;为防止熔体吸入过多的空气,熔化过程应尽可能在短时间内和封闭环境内完成。
[0184] (3)再按配方比例先加入Al-MruAl-T1、Al-Be、Al-Nb、Al_Zr中间合金或者混合金属添加剂(包括盐类化合物),搅拌均匀后再加入Cu纯金属及Al-Cd中间合金或者混合金属添加剂,再加入B和稀土元素Y,搅拌均匀。
[0185] 混合金属添加剂是指添加、调整合金组元用的饼状或块状非烧结性粉末冶金制品,包括锰、铜、锆、铍、铌、硼或钛金属粉末与熔剂混合而成。熔剂是指碱金属或碱土金属卤素盐类的混合物,包括NaCl、KCl和Na3AlF615
[0186] (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂(可根据不同工况采用氯气、六氯乙烷、氯化锰等作为精炼剂,以及硼盐变质剂等),并搅拌均匀,同时为防止熔体吸入水份和烧损,熔体精炼应尽可能在封闭环境中操作。
[0187] (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理。
[0188] (6)铸造(在铸模中结晶凝固)。
[0189] (7)对铸件进行470〜560 V、30小时以内的固溶处理。
[0190] (8)试样指标:抗拉强度487Mpa,延伸率3.9%。
Claims (3)
1.一种Be-Nb-RE高强耐热铝合金材料,其特征在于:按重量百分比计,该合金成分为Cu: 1.0 〜10.0%,Μη:0.05 〜1.5%, Cd:0.01 〜0.5%,T1:0.01 〜0.5%,B:0.01 〜0.2%,Zr:0.01 〜1.0%, Be:0.001 〜0.1%,Nb:0.01 〜1.0%,稀土元素 RE:0.05 〜5%,其余为 Al。
2.根据权利要求1所述的Be-Nb-RE高强耐热铝合金材料,其特征在于:稀土元素RE为单一稀土元素或混合稀土元素。
3.—种如权利要求2所述的Be-Nb-RE高强耐热铝合金材料的制备方法,其特征在于:包括如下步骤: (1)在上述元素比例范围内,选定一组元素比例,再根据需要配制的合金总量,推算出所需的每种单质金属的质量,或者中间合金的质量,编制合金生产配料表,并按配料表选足备料; (2)往熔炼炉中加入适量的铝锭或熔融铝液,加热使之完全熔化并在700〜800°C下保温;熔化过程在封闭环境内完成; (3)再按配方比例先加入 Mn、T1、Zr、Be、Nb 纯金属或 Al-Mn、Al-T1、Al-Zr、Al-Be、Al_Nb中间合金,搅拌均匀后再加入Cu、Cd纯金属或Al-Cu、Al-Cd中间合金,再加入B和稀土元素RE,搅拌均匀; (4)然后对上述合金熔体进行炉内精炼;往合金熔体中加入精炼剂,并搅拌均匀,熔体精炼在封闭环境中操作; (5)精炼后打渣、静置、调温至630〜850°C,合金液倾倒出炉,在线除气、除渣处理; (6)铸造; (7 )对铸件进行470〜56·0 V、30小时以内的固溶处理。
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