JPH01147037A - Heat-resistant al alloy for powder metallurgy - Google Patents
Heat-resistant al alloy for powder metallurgyInfo
- Publication number
- JPH01147037A JPH01147037A JP30153987A JP30153987A JPH01147037A JP H01147037 A JPH01147037 A JP H01147037A JP 30153987 A JP30153987 A JP 30153987A JP 30153987 A JP30153987 A JP 30153987A JP H01147037 A JPH01147037 A JP H01147037A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- weight
- resistant
- heat
- powder metallurgy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 9
- 229910000838 Al alloy Inorganic materials 0.000 title abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 12
- 239000000956 alloy Substances 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 6
- 238000000034 method Methods 0.000 abstract description 8
- 239000000843 powder Substances 0.000 abstract description 8
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 description 7
- 230000007423 decrease Effects 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001125 extrusion Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910019580 Cr Zr Inorganic materials 0.000 description 2
- 229910019817 Cr—Zr Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000001447 compensatory effect Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000003353 gold alloy Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 102000004169 proteins and genes Human genes 0.000 description 1
- 108090000623 proteins and genes Proteins 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 235000014347 soups Nutrition 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
先１上夏且ユ±１
本発明は、高温で強度低下が少なく、熱間加二［性の良
好なる粉末冶金用耐熱△ｊ合金に係り、特に内燃機関の
連接棒およびバルブ（弁）の如く高温に加熱される構造
用部材に好適に使用される耐熱ＡＪ金合金関するもので
ある。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a heat-resistant △j alloy for powder metallurgy, which has little strength loss at high temperatures and has good hot workability. The present invention relates to a heat-resistant AJ gold alloy that is suitably used for structural members that are heated to high temperatures, such as rods and valves.
′１−およびその、１′
耐熱性の優れたＡ」合金として、Ｓλを１８〜２５重量
％も含むピストン用合金（通称、アルシル）が知られて
いる。この高ＳＬ含有、１合金は鋳造用合金であって、
溶解法によれば、■大な初晶Ｓλが晶出して必要な強度
が得られないため、改良処理（例、溶湯中にＮａを添加
する）を１１なって初品Ｓλの微細化を訓っている。し
かしながら、その微細化効果には限界があるところから
、高ＳＬ含有過共晶Ａｊ合金粉末をアトマイジング法で
製造することにより初晶Ｓλの粒仔を数μｍ程度に押え
、その汁粉成形体を熱間押出し加工して高強度の焼結／
１合金製部材を１ｑる方法が１２案されている。この粉
末冶金用ＡＪ）合金では高温強度。'1- and its 1' Piston alloys (commonly known as Arcil) containing 18 to 25% by weight of Sλ are known as A' alloys with excellent heat resistance. This high SL content, 1 alloy is a casting alloy,
According to the melting method, large primary crystals Sλ crystallize and the necessary strength cannot be obtained, so improvement treatment (for example, adding Na to the molten metal) is conducted to refine the initial crystal Sλ. ing. However, there is a limit to its refining effect, so by manufacturing hypereutectic Aj alloy powder with high SL content using the atomizing method, the particle size of primary S High strength sintering by hot extrusion processing/
Twelve methods have been proposed for making one alloy member. This AJ) alloy for powder metallurgy has high temperature strength.
ヤング率を向上させるために２重量％以上のＦｅを添加
しているが、ＡＡ中にＦｅ、Ｓ＝が共存すると針状のＡ
ｊｓ Ｆｅ、Ａｊ１２Ｆｅ３ Ｓ、ｚ等の金題がある。Although 2% by weight or more of Fe is added to improve Young's modulus, if Fe and S= coexist in AA, acicular A
There are gold medals such as js Fe, Aj12Fe3 S, z, etc.
また、近年ＡＪ−Ｆｅ系合金を中心にΔ１−Ｆｅ−Ｃｅ
、Ａｌ１−Ｆｅ−Ｍｏ等の粉末冶金用三元合金が研究さ
れているが、熱間加Ｚ［性が低いという問題が残ってい
る。In addition, in recent years, Δ1-Fe-Ce has been developed mainly in AJ-Fe alloys.
, Al1-Fe-Mo, and other ternary alloys for powder metallurgy have been studied, but the problem of low hot workability remains.
Ｌ＋ を ｌ−るための および本発明は斯かる
技術的前原の下に創案されたものであり、ＳＬを含まな
いがα固溶体に対して溶解限度を越える８の合金元素を
含有する粉末冶金用耐熱Ａｌ合金を１２供することをそ
の目的とする。The present invention has been devised under such technical forerunners, and is intended for use in powder metallurgy, which does not contain SL but contains eight alloying elements whose solubility limit exceeds the solubility limit in α solid solution. The purpose is to provide 12 heat-resistant Al alloys.
この目的は、５≦Ｃｒ≦１２重量％、１≦Ｆｅ≦５重量
％、０．５≦Ｚｒ≦３重量％なる組成範囲のＣｒ、Ｆｅ
、Ｚｒと、不可避不純物を含む残部Ａｌとから成る耐熱
ＡｆＪ合金を提供することによって達成される。This purpose is to use Cr, Fe in the composition range of 5≦Cr≦12% by weight, 1≦Fe≦5% by weight, and 0.5≦Zr≦3% by weight.
, Zr, and the remainder Al containing unavoidable impurities.
粉末冶金法において、ＡＪ中に固溶限界を越えてＣｒお
よびＺｒを添加し、Ａ、Ｑ−Ｃｒ系、ＡＪ！−Ｚｒ系、
Ｃｒ−Ｚｒ系の金属間化合物を微細に分散晶出１分散析
出させると、マトリックス中へのＱｒ、 Ｚｒの固溶に
よる強化および、金属間化合物の晶出、析出による強化
を削ることが可能である。In the powder metallurgy method, Cr and Zr are added in AJ beyond the solid solubility limit to form A, Q-Cr system, AJ! -Zr series,
Finely dispersed crystallization of Cr-Zr intermetallic compounds 1 Disperse precipitation of Cr-Zr intermetallic compounds makes it possible to reduce the strengthening due to solid solution of Qr and Zr in the matrix and the strengthening due to crystallization and precipitation of intermetallic compounds. be.
ここで留意すべきは、前記金属間化合物が粗大化すると
焼結晶の機械的性質が損われるため、溶融状態からの冷
却速度を十分大きくして粉末を製造する必要がある点で
ある。要求される冷却条件は冷却速度１０２〜ｂ
度によって晶出または析出する金属間化合物の大きさを
１０μｍ以）に抑えることができる。It should be noted here that if the intermetallic compound becomes coarse, the mechanical properties of the sintered crystal will be impaired, so it is necessary to manufacture the powder at a sufficiently high cooling rate from the molten state. The required cooling conditions are such that the size of the intermetallic compound that crystallizes or precipitates can be suppressed to 10 .mu.m or less by cooling at a cooling rate of 10.degree. to 10.degree.
ＡＪ中に添加する合金元素の添加理由は以下の通りであ
る。The reason for adding the alloying elements to AJ is as follows.
■Ｃｒ （５〜１２重邑％）・・・Ｃｒは常温強Ｉ！！
および高温強度の向上、クリープ特性の改善を８するた
めに添加される。ただし、５重間％未満では温度３００
〜４００℃における強度が低く、１２重量％を越えると
熱間加工性が低下し、伸び率が過小になる。■Cr (5-12%)...Cr is strong at room temperature! !
It is added to improve high temperature strength and creep properties. However, if the temperature is less than 5%,
The strength at ~400°C is low, and if it exceeds 12% by weight, hot workability decreases and the elongation rate becomes too small.
■「ｅ（１〜５重量％） ・Ｆ ｅは常温強＋ｉ、ｎ温
強度、ヤング率の向上に寄与する。ただし、１重量％未
満では添加効果が小さく、５手量％を越えると切欠き感
受性が高くなり、伸び率が過小になる。■"e (1 to 5% by weight) ・Fe contributes to improving room temperature strength + i, n temperature strength, and Young's modulus. However, if it is less than 1% by weight, the effect of addition is small, and if it exceeds 5% by weight, it will be cut off. Sensitivity to chipping increases and elongation rate becomes too low.
■ｚｒ （０，５〜３ｆｆｉ１％＞−ｚ ｒは、展延性
。■zr (0.5~3ffi1%>-z r is malleability.
クリープ特性を改善するために添加される。ただし、０
．５手量％未満では改善効果が少なく、３手量％を越え
ると展延性が低下する。Added to improve creep properties. However, 0
．． If the amount is less than 5% by weight, the improvement effect will be small, and if it exceeds 3% by weight, the spreadability will decrease.
次に、本発明組成のＡ」合金粉末を用いた焼結晶の製造
方法例について説明する。Next, an example of a method for producing sintered crystals using alloy powder A having the composition of the present invention will be described.
■粉末のＷｌＪ造・・・５≦Ｃｒ≦１２重蛋％、１≦Ｆ
ｅ≦５重量％、０．５≦Ｚｒ≦３重量％なる組成範囲の
Ｃｒ、Ｆｅ、Ｚｒを含むＡｌ合金粉末（粒径１０５μｍ
未満）を、Ｈｅガスを用いたアトマイズ法、遠心噴霧法
等により冷却速度７０２〜ｂ秒なる条件を満たすように
製造する。■ Powder WlJ construction...5≦Cr≦12 heavy protein%, 1≦F
Al alloy powder containing Cr, Fe, and Zr with a composition range of e≦5% by weight and 0.5≦Zr≦3% by weight (particle size 105 μm)
) is manufactured by an atomization method using He gas, a centrifugal spraying method, etc. so as to satisfy the condition of a cooling rate of 702 to b seconds.
■汁粉成形・・・得られた粉末を、冷間静水圧プレス成
形法（ＣＩＰ法）により圧力４ 、００ＯＮｙ ｆｏｃ
ｉとして、寸法５０ｍφＸ １００ｍの押出し加工用素
材を得る。■Soup powder molding: The obtained powder is subjected to cold isostatic press molding (CIP method) under a pressure of 4,000 ONy foc.
As i, a material for extrusion processing with dimensions of 50 mφ x 100 m is obtained.
■熱間押出し加：［（焼結）・・・圧粉体である押出し
加工用石材を、温度４５０℃、押出し比１２なる条件で
熱間押出し加工する。なお、成形品の酸化防止を考慮す
るならば、アルゴンガス、窒素ガス等の非酸化性雰囲気
中で加工を行うのが好ましい。■Hot extrusion: [(Sintering)... Stone for extrusion, which is a green compact, is hot extruded at a temperature of 450°C and an extrusion ratio of 12. Note that in consideration of preventing oxidation of the molded product, it is preferable to perform the processing in a non-oxidizing atmosphere such as argon gas or nitrogen gas.
人−翌−１
前記製造方法に則って得た本発明例としての焼結晶（Ａ
、Ｂ）および同様な方法で得た比較例としての焼結晶（
ａ、ｂ、Ｃ，ｄ、ｅ、ｆ）にライて引張り試験を行い、
取去の試験結果を得た。表中熱間加工性について、試験
材である焼結晶を押出し加工によって製造する際の割れ
の有無で判断した。Person - Next day - 1 Sintered crystal (A
, B) and a sintered crystal as a comparative example obtained by the same method (
a, b, C, d, e, f) and conducted a tensile test,
Removal test results were obtained. The hot workability in the table was judged by the presence or absence of cracks when the test material, sintered crystal, was manufactured by extrusion processing.
く試験結果の評価〉
■比較例ａ、ｂ、ｃの対比から、Ｃｒ吊が増すと、常温
および３００℃における引張り強度が向上し、伸び率が
低下することが判る。特に、Ｃｒｆｌが１２重間％を越
えた１５重量％では著しく伸び率が低下しており、熱間
加工性が不良である。Evaluation of Test Results> ■ A comparison of Comparative Examples a, b, and c shows that as the Cr suspension increases, the tensile strength at room temperature and 300° C. improves, and the elongation rate decreases. In particular, when the Crfl content exceeds 12% by weight (15% by weight), the elongation rate decreases significantly and the hot workability is poor.
■比較例ａ、ｂ、ｃ、ｄ、ｅの対比から、常温および高
温での引張り強度を向上さゼるためにＦｅの添加が有効
であり、その効果はｃｒの添加による効果に比して大き
いことが判る。ただし、Ｆｅの添加は伸び率を低下させ
、特にＦｅｆｆ１が５重量％を越える６重ω％では著し
く伸び率が低下し、熱間加工性が不良である。■From the comparison of Comparative Examples a, b, c, d, and e, the addition of Fe is effective in improving the tensile strength at room temperature and high temperature, and its effect is compared to the effect of adding Cr. It turns out it's big. However, the addition of Fe lowers the elongation rate, and especially when Feff1 exceeds 5% by weight, the elongation rate decreases significantly and the hot workability is poor.
■比較例ｄ、ｆ、本発明例Ａ、Ｂの対比から、Ｆｅの添
加により低下する伸び特性および熱間加工性をＺｒの添
加によって補償し得ることが判る。(2) A comparison of Comparative Examples d and f and Invention Examples A and B shows that the elongation properties and hot workability deteriorated by the addition of Fe can be compensated for by the addition of Zr.
ただし、Ｚｒ添加量が３重量％を越える５重間％では、
伸び特性、熱間加工性に及ぼすｚｒの補償効果はなくな
る。また、Ｚｒを添加すると、常温および高温における
引張り強度が向上することが判る。ただし、Ｚｒ添加量
が３重量％を越える５重量％では引張り強度が若干低下
する。However, when the amount of Zr added exceeds 3% by weight,
The compensatory effect of Zr on elongation properties and hot workability disappears. It is also found that adding Zr improves the tensile strength at room temperature and high temperature. However, when the amount of Zr added exceeds 3% by weight and is 5% by weight, the tensile strength slightly decreases.
■全試験材の対比から、規定量のＣｒ、 Ｆｅ。■From the comparison of all test materials, the specified amount of Cr and Fe.
Ｚｒを添加した本発明例では、常温および高温（３００
℃）における引張り強度が十分大きく、適度の伸び率と
、良好な熱間加工性を確保し得ることが判る。In the example of the present invention in which Zr is added, the temperature at room temperature and high temperature (300
It can be seen that the tensile strength at temperature (°C) is sufficiently high, and a suitable elongation rate and good hot workability can be ensured.
１団夏盈」
以上の説明から明らかなように、５≦Ｃｒ≦１２重量％
、１≦Ｆｅ≦５重ｉ％、０．５≦Ｚｒ≦３重量％なる組
成範囲のＣｒ、Ｆｅ、Ｚｒと、不可避不純物を含む残部
Ａｌとから成る粉末冶金用耐熱ＡＮ合金が提案された。As is clear from the above explanation, 5≦Cr≦12% by weight
, 1≦Fe≦5 i% by weight, 0.5≦Zr≦3% by weight, and a heat-resistant AN alloy for powder metallurgy consisting of Cr, Fe, and Zr in the composition range, and the balance containing inevitable impurities has been proposed.
この組成範囲の合金は、常温における引張り強度が十分
大きく、温度３００℃においても約３０Ｋｙｆ／Ｍ２以
上の大きな引張り強度を有し、しかも展延性、熱間加工
性共に良好である。An alloy in this composition range has a sufficiently high tensile strength at room temperature, a high tensile strength of about 30 Kyf/M2 or more even at a temperature of 300° C., and has good malleability and hot workability.
Claims (1)
Ｚｒ≦３重量％なる組成範囲のＣｒ，Ｆｅ，Ｚｒと、不
可避不純物を含む残部Ａｌとから成る粉末冶金用耐熱Ａ
ｌ合金。5≦Cr≦12% by weight, 1≦Fe≦5% by weight, 0.5≦
Heat-resistant A for powder metallurgy consisting of Cr, Fe, and Zr in a composition range of Zr≦3% by weight, and the remainder Al containing unavoidable impurities
l alloy.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP30153987A JPH01147037A (en) | 1987-12-01 | 1987-12-01 | Heat-resistant al alloy for powder metallurgy |
| CA000584522A CA1330400C (en) | 1987-12-01 | 1988-11-30 | Heat-resistant aluminum alloy sinter and process for production of the same |
| EP88311390A EP0319295B1 (en) | 1987-12-01 | 1988-12-01 | Heat-resistant aluminum alloy sinter and process for production of the same |
| DE3888308T DE3888308T2 (en) | 1987-12-01 | 1988-12-01 | Heat-resistant, sintered aluminum alloy and process for its production. |
| US07/278,581 US5022918A (en) | 1987-12-01 | 1988-12-01 | Heat-resistant aluminum alloy sinter and process for production of the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP30153987A JPH01147037A (en) | 1987-12-01 | 1987-12-01 | Heat-resistant al alloy for powder metallurgy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01147037A true JPH01147037A (en) | 1989-06-08 |
Family
ID=17898154
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP30153987A Pending JPH01147037A (en) | 1987-12-01 | 1987-12-01 | Heat-resistant al alloy for powder metallurgy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01147037A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01147038A (en) * | 1987-12-02 | 1989-06-08 | Honda Motor Co Ltd | Heat-resistant al alloy for powder metallurgy |
| JPH01149936A (en) * | 1987-12-04 | 1989-06-13 | Honda Motor Co Ltd | Heat-resistant al alloy for powder metallurgy |
| JPH02194142A (en) * | 1989-01-21 | 1990-07-31 | Kobe Steel Ltd | Al-base alloy powder for sintering |
| CN106086719A (en) * | 2016-07-28 | 2016-11-09 | 吴国庆 | A kind of high heat-resisting nickel-copper alloy material and preparation method thereof |
-
1987
- 1987-12-01 JP JP30153987A patent/JPH01147037A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01147038A (en) * | 1987-12-02 | 1989-06-08 | Honda Motor Co Ltd | Heat-resistant al alloy for powder metallurgy |
| JPH01149936A (en) * | 1987-12-04 | 1989-06-13 | Honda Motor Co Ltd | Heat-resistant al alloy for powder metallurgy |
| JPH02194142A (en) * | 1989-01-21 | 1990-07-31 | Kobe Steel Ltd | Al-base alloy powder for sintering |
| CN106086719A (en) * | 2016-07-28 | 2016-11-09 | 吴国庆 | A kind of high heat-resisting nickel-copper alloy material and preparation method thereof |
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