JPH01149936A - Heat-resistant al alloy for powder metallurgy - Google Patents
Heat-resistant al alloy for powder metallurgyInfo
- Publication number
- JPH01149936A JPH01149936A JP30590487A JP30590487A JPH01149936A JP H01149936 A JPH01149936 A JP H01149936A JP 30590487 A JP30590487 A JP 30590487A JP 30590487 A JP30590487 A JP 30590487A JP H01149936 A JPH01149936 A JP H01149936A
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- JP
- Japan
- Prior art keywords
- alloy
- weight
- heat
- less
- 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.)
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Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 16
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 13
- 238000005275 alloying Methods 0.000 claims abstract description 28
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 13
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 12
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 10
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 10
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 4
- 239000002245 particle Substances 0.000 claims description 14
- 239000012535 impurity Substances 0.000 claims description 6
- 239000011159 matrix material Substances 0.000 claims description 5
- 229910052746 lanthanum Inorganic materials 0.000 claims 1
- 229910052758 niobium Inorganic materials 0.000 claims 1
- 239000000843 powder Substances 0.000 abstract description 10
- 239000000203 mixture Substances 0.000 abstract description 7
- 238000001816 cooling Methods 0.000 abstract description 5
- 238000001192 hot extrusion Methods 0.000 abstract description 3
- 238000002485 combustion reaction Methods 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000956 alloy Substances 0.000 description 19
- 229910045601 alloy Inorganic materials 0.000 description 18
- 239000000463 material Substances 0.000 description 15
- 230000000052 comparative effect Effects 0.000 description 12
- 238000000034 method Methods 0.000 description 8
- 238000009792 diffusion process Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- 239000007787 solid Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- DASQRZJTRKBKPP-UHFFFAOYSA-N 5-butan-2-yl-2-(2,4-dimethylcyclohex-3-en-1-yl)-5-methyl-1,3-dioxane Chemical compound O1CC(C(C)CC)(C)COC1C1C(C)C=C(C)CC1 DASQRZJTRKBKPP-UHFFFAOYSA-N 0.000 description 1
- 229910001316 Ag alloy Inorganic materials 0.000 description 1
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 101000685083 Centruroides infamatus Beta-toxin Cii1 Proteins 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052757 nitrogen 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
- 229910052697 platinum Inorganic materials 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
ＩＬ上立旦皿±１
本発明は、高温で強度低下が少なく、熱間加工性の良好
なる粉末冶金用耐熱Ａｌ合金に係り、特に内燃機関の連
接棒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Ａ９合金に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a heat-resistant Al alloy for powder metallurgy, which exhibits little strength loss at high temperatures and has good hot workability, particularly when used in high-temperature applications such as connecting rods of internal combustion engines. The present invention relates to a heat-resistant A9 alloy that is suitably used for structural members that are heated.
−のｐ
耐熱性の優れたＡｌ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８＝含有Ａｌ１合金は鋳造用合金であって
、鋳造法によれば、粗大な初晶ＳＬが晶出して必要な強
度が得られないため、改良処理〈例、溶場中にＮａを添
加する）を行なって初晶Ｓλ粉粒子微細化を計っている
。しかしながら、その微細化効果には限界があり、また
溶解法により得たＡ９合金は温度１５０℃以上で急速に
軟化するという弱点があるところから、高ＳＬ含有過共
晶ＡｆＪ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ＳＬの粒径を数μｍ程度に抑え、その圧粉成形
体を熱間押出し加工して高強度のＡｌ合金焼結材を得る
方法が提案されている。- p As an Al alloy with excellent heat resistance, a piston alloy (commonly known as Alsil) containing 18 to 25% by weight of Sλ is known. This high 8 = Al1 alloy is a casting alloy, and according to the casting method, coarse primary crystals SL crystallize and the necessary strength cannot be obtained. (addition)) to refine the primary crystal Sλ powder particles. However, there are limits to its refinement effect, and the A9 alloy obtained by the melting method has the disadvantage of rapidly softening at temperatures above 150°C. A method has been proposed in which the particle size of the primary crystal SL is suppressed to about several μm by manufacturing, and the compacted product is hot extruded to obtain a high-strength Al alloy sintered material.
例えば、この方法によって得た１ｌ−８Ｆｅ系合金焼結
材は耐熱性良好であり、温度２００℃で３０ｋｇｆ／ｍ
ｍ２に達する引張り強度を有している。For example, the 1l-8Fe based alloy sintered material obtained by this method has good heat resistance, and is 30 kgf/m at a temperature of 200°C.
It has a tensile strength of up to m2.
を ° るための よび
本発明は斯かる技術的背景の下に創案されたものであり
、その目的は粉末冶金法によりへ１−８Ｆｅ系合金より
も更に優れた耐熱性を有するＡＪＩ合金を提供すること
である。The present invention was devised against this technical background, and its purpose is to provide an AJI alloy that has even better heat resistance than 1-8Fe alloys by powder metallurgy. It is to be.
この目的は、■Ｃｒを３〜２０重間％、 Ｆｅ。This purpose is: ■ 3 to 20% by weight of Cr and Fe.
Ｔ、ｔ、Ｇｏ、ＮＬ、ｖ、Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ。T, t, Go, NL, v, Ce, Mo, La, Nb.
Ｙ、Ｈｆからなる群より選ばれた一種の合金元素を１０
重量％未満または二種以上の合金元素を計１０重量％未
満含有し、残部が不可避不純物と１１であることを特徴
とする粉末冶金用耐熱ＡｆＪ合金、および■Ｃｒを３〜
２０重世％、 Ｚｒ、 Ｍｎのうち一方の合金元素を７
１四％未満または両合金元素を７重量％未満、Ｆｅ、Ｔ
＝、Ｃｏ、Ｎｉ、Ｖ。10 types of alloying elements selected from the group consisting of Y and Hf
A heat-resistant AfJ alloy for powder metallurgy, characterized in that it contains less than 10% by weight or less than 10% by weight of two or more alloying elements, with the balance being unavoidable impurities and 11%, and
20%, one of the alloying elements of Zr and Mn is 7%
Less than 14% or less than 7% by weight of both alloying elements, Fe, T
=, Co, Ni, V.
Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ、Ｙ、Ｈｆからなる群より選ば
れた一種の合金元素を１０重０％未満または二種以上の
合金元素を計１０重伍％未満含有し、残部が不可避不純
物とＡｌであることを特徴とする粉末冶金用耐熱Ａｌ合
金を提供することによって達成される。Contains less than 10% by weight of one alloying element selected from the group consisting of Ce, Mo, La, Nb, Y, and Hf, or less than 10% by weight in total of two or more alloying elements, with the remainder being unavoidable impurities. This is achieved by providing a heat-resistant Al alloy for powder metallurgy, which is characterized by being made of Al.
粉末冶金法において、Ａ、ｌＩ中に固溶限界を越えてＣ
ｒ、Ｆｅ、Ｔｔ等の合金元素を添加し、該合金元素とＡ
ｌとの金属間化合物を微細に分散品出。In powder metallurgy, C exceeds the solid solubility limit in A and I.
By adding alloying elements such as r, Fe, and Tt, the alloying elements and A
A product with finely dispersed intermetallic compounds.
分散析出させると、マトリックス中へのＯｒ。When dispersed and precipitated, Or into the matrix.
Ｆｅ、Ｔｔ等の固溶による強化および金属間化合物粒子
の晶出、析出による強化を計ることが可能である。しか
るに、析出した金属間化合物粒子は常温で安定であるも
のの、温度上昇とともにマトリックス中に固溶し、金属
間化合物粒子の析出による硬化効果は次第に失われる。It is possible to strengthen by solid solution of Fe, Tt, etc. and by crystallization or precipitation of intermetallic compound particles. However, although the precipitated intermetallic compound particles are stable at room temperature, as the temperature rises, they become solid dissolved in the matrix, and the hardening effect due to the precipitation of the intermetallic compound particles is gradually lost.
その際、マトリックス中への金属間化合物粒子の固溶速
度は主として合金元素のＡｌ中での拡散係数（ＣＩＩ１
２７秒）に依存する。すなわち、Ａｌ合金焼結材の耐熱
性を向上させるためには、拡散係数が小さく、かつ固溶
限界の小さな金属間化合物形成元素を添加する必要があ
る。拡散係数の小さい合金元素の代表例４；ｔｃｒ（Ａ
ｊ中テノ拡散係数＝ １０−” 〜１０−”Ｃ１１２／
秒）であり、Ｃｒの添加によってＡ９合金の耐熱性が向
上する。この他、Ａｊ中での拡散係数。At that time, the solid solution rate of intermetallic compound particles in the matrix is mainly determined by the diffusion coefficient of alloying elements in Al (CII1
27 seconds). That is, in order to improve the heat resistance of the sintered Al alloy material, it is necessary to add an intermetallic compound-forming element that has a small diffusion coefficient and a small solid solubility limit. Representative example 4 of alloying elements with small diffusion coefficient; tcr(A
j medium teno diffusion coefficient = 10-” ~10-”C112/
sec), and the addition of Cr improves the heat resistance of the A9 alloy. In addition, the diffusion coefficient in Aj.
固溶限界が小さい元素として、Ｚｒ、 Ｍｎ、 Ｆｅ。Zr, Mn, and Fe are elements with small solid solubility limits.
Ｔ、ｔ、Ｇｏ、ＮＬ、Ｖ、Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ。T, t, Go, NL, V, Ce, Mo, La, Nb.
Ｙ、Ｈｆ等を挙げることができ、これ等はいずれもＡｌ
合金の耐熱性を向上させる。Examples include Y, Hf, etc., which are all Al
Improves the heat resistance of the alloy.
なお、留意すべきは、前記金属間化合物が粗大化すると
Ａｌ１合金焼結材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ぎくして粉末を製造すべき点
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される金属間化合物の大きさ
を１０μｍ以下に抑えることができる。It should be noted that if the intermetallic compound becomes coarse, the mechanical properties of the Al1 alloy sintered material will be impaired, so the cooling rate from the molten state should be sufficiently increased to produce the powder. The required cooling conditions are such that the cooling rate is 102 to 100°C, so that the size of intermetallic compounds that are crystallized or precipitated can be suppressed to 10 μm or less.
Ａｊｌ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 Ajl is as follows.
■Ｃｒ （３〜２０重量％）・・・Ｃｒは必須添加成分
であり、常温強度および高温強度の向上、クリープ特性
の改善を計るために添加される。ただし、３重Ｄ％未満
では常温および２００℃での強度が低く（引張り強度＜
３０ｋｇｆ／ｍｎ＋２） 、２０重量％を越えると展延
性が低下し、熱間加工が難しくなる。(2) Cr (3 to 20% by weight) Cr is an essential additive component, and is added to improve the room temperature strength and high temperature strength, as well as the creep properties. However, if it is less than 3x D%, the strength at room temperature and 200°C is low (tensile strength <
30kgf/mn+2), exceeding 20% by weight, the malleability decreases and hot working becomes difficult.
■Ｆｅ、Ｔｚ、 ｃｏ等−Ｆ ｅ 、 Ｔ Ｌ、 Ｇ
Ｏ。■Fe, Tz, co, etc. - Fe, T L, G
O.
Ｎｉ、Ｖ、Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ、Ｙ、Ｈｆは常温強
度、高温強度の向上に寄与する。ただし、過剰添加は展
延性を阻害し、熱間加工を困難にする。前記合金元素の
うちの一種または二種以上の総添加ｍは１０重０％未満
にすべきであり、この範囲を越えると展延性が損われる
。Ni, V, Ce, Mo, La, Nb, Y, and Hf contribute to improving room temperature strength and high temperature strength. However, excessive addition inhibits malleability and makes hot working difficult. The total addition m of one or more of the alloying elements should be less than 10% by weight, and if this range is exceeded, malleability will be impaired.
■Ｍｎ、Ｚｒ・Ｚｒ、Ｍｎ、Ｆｅ、Ｔ＝、Ｇｏ。■Mn, Zr・Zr, Mn, Fe, T=, Go.
ＮＬ、ｖ、Ｃｅ、ＭＯ，Ｌａ、Ｎｂ、Ｙ、Ｈｆのうち、
その二種以上を添加した場合に添加元素同志で金属間化
合物を形成するものとしてＭｎ。Among NL, v, Ce, MO, La, Nb, Y, Hf,
Mn forms an intermetallic compound with the added elements when two or more of them are added.
Ｚｒ、Ｆｅ、 ＮＬ、Ｇｏ等を揚げ得るが、Ｍｎ。Zr, Fe, NL, Go, etc. can be fried, but Mn.
Ｚｒは、本発明合金における必須添加成分であるＣｒと
も金属間化合物を形成するため、他の合金元素に比して
少量（７重量％未満）にて析出強化を計り得る反面、過
剰のＭｎ、Ｚｒは著しく伸び率を低下させる。故に、Ｍ
ｎ、Ｚｒの一方または両方の上限添加量を７重量％未満
とする。Since Zr forms an intermetallic compound with Cr, which is an essential additive component in the alloy of the present invention, precipitation strengthening can be achieved with a small amount (less than 7% by weight) compared to other alloying elements, but excessive Mn, Zr significantly reduces the elongation rate. Therefore, M
The upper limit addition amount of one or both of n and Zr is less than 7% by weight.
次に、本発明組成のＡｇ合金粉末を用いた焼結材の製造
方法例について説明する。Next, an example of a method for producing a sintered material using the Ag alloy powder having the composition of the present invention will be described.
■粉末の製造・・・本発明組成のＡｌ合金粉末（粒径１
０５μｍ未ｉ＞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１０２〜ｂ／秒なる条件を満
たすように製造する。■Production of powder...Al alloy powder of the composition of the present invention (particle size 1
05 μm <i> is manufactured by an atomization method using He gas, a centrifugal spray method, etc. so as to satisfy the condition of a cooling rate of 10 2 -b/sec.
■圧粉成形・・・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．ＯＯＯｋｇｆ／ｃｍ
２として、寸法５０ｍＩＩｌφｘ １００ｍｒｎの押出
し加工用素材を得る。■Powder compacting: The obtained powder is subjected to cold isostatic press molding (CIP method) at a pressure of 4. OOOkgf/cm
As No. 2, a material for extrusion processing with dimensions of 50 mIIlφx 100 mrn was obtained.
■熱間押出し加工（焼結）・・・圧粉体である押出し加
工用素材を炉内温度４５０℃の均熱炉内に設置し、１時
間保持して脱ガスを行い、次いで温度４５０℃、押出し
比１４なる条件で熱間押出し加工を行う。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 processing (sintering)...The extrusion processing material, which is a green compact, is placed in a soaking furnace with an internal temperature of 450°C, held for 1 hour to degas, and then heated to 450°C. , hot extrusion processing is carried out under the conditions of extrusion ratio 14. 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.
隨１拠ユ
前記製造方法に則って得た本発明例としての焼結材（Ａ
：特許請求の範囲第１項の発明に対応）（表１）、（Ｂ
、Ｃ，Ｄ、Ｅ、Ｆ：特許請求の範囲第２項の発明に対応
）（表１）および同様な方法で得た比較例としての焼結
材（ａ、ｂ、ｃ、ｄ。Sintered material (A) as an example of the present invention obtained according to the above manufacturing method
: Corresponds to the invention in claim 1) (Table 1), (B
, C, D, E, F: corresponding to the invention of claim 2) (Table 1) and sintered materials as comparative examples obtained by the same method (a, b, c, d).
ｅ）（表１）について引張り試験を行い、表２の試験結
果を得た。表中、評価欄の“ＯＩ＋は温度２００℃にお
ける引張り強度が３０ｋｇｆ／ｍｍ”以上であり、伸び
率が１％を越えて熱間加工性が良好であるものを示し、
前記引張り強度条件を満たさないが他の条件を満たすも
のを△”、前記全ての条件を満たさないものを×″とし
た。e) A tensile test was conducted on (Table 1), and the test results in Table 2 were obtained. In the table, "OI+" in the evaluation column indicates that the tensile strength at 200 ° C. is 30 kgf/mm or more, the elongation rate is more than 1%, and the hot workability is good.
Those that did not meet the above tensile strength conditions but satisfied other conditions were rated △", and those that did not meet all of the above conditions were rated x".
（以下、余白）
表１
表２
く試験結果の評価〉
■本発明例（Ａ、８．Ｃ，Ｄ、Ｅ、Ｆ、Ｇ、ト１゜りと
比較例（ａ、ｂ、ｃ、ｄ、ｅ、ｆ、ｇ、ｈ。(The following are blank spaces) Table 1 Table 2 Evaluation of test results> ■ Inventive examples (A, 8. e, f, g, h.
ｉ）との対比から、本発明組成範囲の合金は晶出物、析
出物の粒径が小さく、常ｌ、 ２００℃における強度
が十分大きいことが判る。温度３００℃においては、本
発明例（Ｂ）を除く他の全ての本発明組成範囲の合金が
３０ｋｇｆ／ａｍ２以上の引張り強度を有している。ま
た、本発明例は伸び率が１％を越えており、熱間加工性
も良好であった。From comparison with i), it can be seen that the alloys within the composition range of the present invention have small grain sizes of crystallized substances and precipitates, and have sufficiently high strength at 200°C. At a temperature of 300° C., all alloys in the composition range of the present invention except for Inventive Example (B) have a tensile strength of 30 kgf/am 2 or more. Moreover, the elongation rate of the present invention example exceeded 1%, and the hot workability was also good.
■本発明例（Ａ）と比較例（ａ）との対比から、規定範
囲のＣｒを含み、Ｍｎ、 Ｚｒを含まないものにおいて
、Ｆｅ、ＴＬの添加が常温、２００℃。(2) Comparing Inventive Example (A) and Comparative Example (a), it was found that Fe and TL were added at room temperature and 200°C in those containing Cr in the specified range but not Mn and Zr.
３００℃における十分大きな引張り強度を与えることが
判る。It can be seen that a sufficiently large tensile strength at 300°C is provided.
■比較例（ａ、 ｂ）から、Ｚｒ、 Ｍｎの添加が常温
。■From comparative examples (a and b), Zr and Mn were added at room temperature.
２００℃、３００℃における引張り強度の向上に有効で
あることが判る。It can be seen that this is effective in improving the tensile strength at 200°C and 300°C.
■本発明例（Ｈ，Ｉ）と比較例（１）との対比からＺｒ
、Ｍｎを過剰添加（７重量％以上）すると著しく脆化す
ることが判る。■ From the comparison between the invention examples (H, I) and comparative example (1), Zr
, it can be seen that excessive addition of Mn (7% by weight or more) causes significant embrittlement.
■本発明例（Ｂ、 Ｃ、Ｇ）から、Ｃｒｆｆ１が増すと
許容範囲内で伸び率が低下するものの、常温から高温に
到る温度範囲で引張り強度が大幅に向上することが判る
。(2) From the inventive examples (B, C, and G), it can be seen that as Crff1 increases, the elongation rate decreases within the allowable range, but the tensile strength significantly improves in the temperature range from room temperature to high temperature.
■本発明例（Ｂ）と比較例（ｂ）との対比から、規定範
囲のＣｒを含み、Ｍｎ、 ｚｒを含むものにおいて、Ｔ
Ｌの添加により常温から高温に到る温度範囲で引張り強
度が若干向上し、伸び率が向上することが判る。■From the comparison between the present invention example (B) and the comparative example (b), it is found that in those containing Cr in the specified range and Mn and zr, T
It can be seen that the addition of L slightly improves the tensile strength and the elongation rate in the temperature range from room temperature to high temperature.
■本発明例（Ｃ）と比較例（Ｃ）との対比から、添加元
素量が同一であっても晶出物、析出物の粒径が過大（溶
解材における晶出物、析出物の粒径と同程度）であると
著しく脆化することが判る。■A comparison between the inventive example (C) and the comparative example (C) shows that even if the amount of added elements is the same, the particle size of crystallized substances and precipitates is excessive (grains of crystallized substances and precipitates in the melted material). It can be seen that if the diameter is about the same as the diameter), it becomes extremely brittle.
■比較例（ｆ）から、Ｍｎ、ｚｒを含んでもＣｒ量が３
重量％未満では伸び率が極めて大きいものの、常温から
高温（３００℃）に到る温度範囲での必要な引張り強度
が得られないことが判る。■From comparative example (f), even if Mn and zr are included, the Cr content is 3.
It can be seen that if the elongation is less than % by weight, the elongation rate is extremely high, but the necessary tensile strength in the temperature range from room temperature to high temperature (300° C.) cannot be obtained.
■比較例（ａ、 ｂ）から、Ｃｒ以外の合金元素を添加
しなければ伸び率は大きいものの、常温から高温（３０
０℃）に到る温度範囲での必要な引張り強度が得られな
いことが判る。■Comparative examples (a, b) show that if alloying elements other than Cr are not added, the elongation rate is high, but at room temperature to high temperature (30
It can be seen that the necessary tensile strength cannot be obtained in the temperature range down to 0°C.
■比較例（ｄ、 ｅ）から、Ｏｒ添加量が過剰であると
著しく脆化することが判る。■Comparative Examples (d, e) show that excessive addition of Or causes significant embrittlement.
■比較例（ａ、 ｈ）から、Ｍｎ、Ｚｒの有無にかかわ
らずＣｒ以外の合金元素（Ｆｅ、Ｔ＝等）の総添加量が
１０重量％以上になると著しく脆化することが判る。② Comparative Examples (a, h) show that irrespective of the presence or absence of Mn and Zr, when the total amount of alloying elements other than Cr (Fe, T=, etc.) added exceeds 10% by weight, significant embrittlement occurs.
１簾■ユ
前述の製造方法に則って得た本発明例としての焼結材（
特許請求の範囲第１項に記載された発明に対応するもの
・・・Ｂ、Ｄ、！、特許請求の範囲第３項に記載された
発明に対応するもの・・・Ａ、Ｃ。1 Sintered material as an example of the present invention obtained according to the above-mentioned manufacturing method (
What corresponds to the invention stated in claim 1...B, D,! , those corresponding to the invention described in claim 3...A, C.
Ｅ、Ｆ、Ｇ、Ｈ，Ｊ）および同様な方法で得た比較例と
しての焼結材（ａ）につき、未熱処理材と熱処理材（温
度３００℃で１００時間保持したもの）との硬度（Ｈｍ
Ｖ）を調べ、これを表３に示した。E, F, G, H, J) and the sintered material (a) as a comparative example obtained by the same method, the hardness ( Hm
V) was investigated and shown in Table 3.
（以下、余白）
表３
く試験結果の評価〉
本発明例（Ａ−Ｊ）と比較例（ａ）との対比から、Ｃｒ
以外の合金元素の添加によって非熱処理材および熱処理
材の硬度が向上しており、該合金元素の添加により析出
硬化効果を期待でき、高温加熱によってもその効果が然
程失われないことが判る。加熱による析出硬化効果の低
下率が特に小さい試験材（好ましいもの）はＡ、Ｈ，Ｊ
である。(Hereinafter, blank space) Table 3 Evaluation of test results> From the comparison between the inventive example (A-J) and the comparative example (a), it was found that Cr
The hardness of the non-heat-treated material and the heat-treated material is improved by the addition of other alloying elements, and it can be seen that the precipitation hardening effect can be expected by adding the alloying element, and that this effect is not significantly lost even by high-temperature heating. The test materials (preferred materials) that have a particularly small rate of decrease in precipitation hardening effect due to heating are A, H, and J.
It is.
１旦五ｌ」
以上の説明から明らかなように、Ｃｒを３〜２０重量％
、Ｆｅ、Ｔｉ、Ｃｏ、Ｎｉ、Ｖ、Ｃｅ。As is clear from the above explanation, 3 to 20% by weight of Cr
, Fe, Ti, Co, Ni, V, Ce.
ＭＯ，Ｌ ａ、 Ｎ ｂ、 Ｙ、 Ｈｆ カラナルＩＪ
にす３！Ｈｆれた一種の合金元素を１０重量％未満また
は二種以上の合金元素をＨ１１０重橙％未満含有し、残
部が不可避不純物とΔｇであることを特徴とする粉末冶
金用耐熱へ１白金、および■Ｃｒを３〜２０重量％。MO, La, N b, Y, Hf Karanal IJ
Nisu 3! 1 Platinum for heat-resistant powder metallurgy characterized by containing less than 10% by weight of one type of alloying element or less than 110% by weight of two or more alloying elements, with the balance being unavoidable impurities and Δg, and ■3 to 20% by weight of Cr.
Ｚｒ、Ｍｎのうち一方の合金元素を７重量％未満または
両合金元素を７重間％未満、Ｆｅ、ＴＬ。One of the alloying elements of Zr and Mn is less than 7% by weight, or both alloying elements are less than 7% by weight, Fe, TL.
Ｃｏ、ＮＬ、Ｖ、Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ、Ｙ。Co, NL, V, Ce, Mo, La, Nb, Y.
Ｈｆからなる群より選ばれた一種の合金元素を１０重量
％未満または二種以上の合金元素を計１０重口％未満含
有し、残部が不可避不純物とＡＩであることを特徴とす
る粉が提案された。A powder is proposed that contains less than 10% by weight of one alloying element selected from the group consisting of Hf or less than 10% by weight of two or more alloying elements, with the balance being unavoidable impurities and AI. It was done.
この組成範囲の合金は、常温から温度２００℃に到る温
度範囲で十分な強度を有し、特に特許請求の範囲第３項
に記載された合金は温度３００℃においても３０ｋｇｆ
／ｍｍ”以上の大きな引張り強度を有しており、また特
許請求請求の範囲第１項、第３項に記載されたいずれの
合金も展延性良好である。The alloy in this composition range has sufficient strength in the temperature range from room temperature to 200°C, and in particular, the alloy described in claim 3 has a strength of 30 kgf even at a temperature of 300°C.
/mm'' or more, and both of the alloys described in Claims 1 and 3 have good malleability.
Claims (4)
、Ｖ、Ｃｅ、Ｍｏ、Ｌａ、Ｎｂ、Ｙ、Ｈｆからなる群よ
り選ばれた一種の合金元素を１０重量％未満または二種
以上の合金元素を計１０重量％未満含有し、残部が不可
避不純物とＡｌであることを特徴とする粉末冶金用耐熱
Ａｌ合金。(1) 3 to 20% by weight of Cr, Fe, Ti, Co, Ni
, V, Ce, Mo, La, Nb, Y, Hf, or less than 10% by weight of two or more alloying elements, with the remainder being unavoidable impurities. A heat-resistant Al alloy for powder metallurgy, characterized by comprising: and Al.
出粒子および析出粒子が粒径１０μｍ以下であることを
特徴とする特許請求の範囲第１項に記載された粉末冶金
用耐熱Ａｌ合金。(2) The heat-resistant Al alloy for powder metallurgy according to claim 1, wherein the crystallized particles and precipitated particles of the intermetallic compound present in the matrix have a particle size of 10 μm or less.
合金元素を７重量％未満または両合金元素を７重量％未
満、Ｆｅ、Ｔｉ、Ｃｏ、Ｎｉ、Ｖ、Ｃｅ、Ｍｏ、Ｌａ、
Ｎｂ、Ｙ、Ｈｆからなる群より選ばれた一種の合金元素
を１０重量％未満または二種以上の合金元素を計１０重
量％未満含有し、残部が不可避不純物とＡｌであること
を特徴とする粉末冶金用耐熱Ａｌ合金。(3) 3 to 20% by weight of Cr, less than 7% by weight of one of Zr and Mn or less than 7% of both alloying elements, Fe, Ti, Co, Ni, V, Ce, Mo, La ,
It is characterized by containing less than 10% by weight of one type of alloying element selected from the group consisting of Nb, Y, and Hf, or less than 10% by weight in total of two or more types of alloying elements, with the balance being unavoidable impurities and Al. Heat-resistant Al alloy for powder metallurgy.
出粒子および析出粒子が粒径１０μｍ以下であることを
特徴とする特許請求の範囲第３項に記載された粉末冶金
用耐熱Ａｌ合金。(4) The heat-resistant Al alloy for powder metallurgy according to claim 3, wherein the crystallized particles and precipitated particles of the intermetallic compound present in the matrix have a particle size of 10 μm or less.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP30590487A JPH01149936A (en) | 1987-12-04 | 1987-12-04 | 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 |
| US07/278,581 US5022918A (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. |
| EP88311390A EP0319295B1 (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 |
|---|---|---|---|
| JP30590487A JPH01149936A (en) | 1987-12-04 | 1987-12-04 | Heat-resistant al alloy for powder metallurgy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01149936A true JPH01149936A (en) | 1989-06-13 |
Family
ID=17950699
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP30590487A Pending JPH01149936A (en) | 1987-12-01 | 1987-12-04 | Heat-resistant al alloy for powder metallurgy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01149936A (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0234740A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| JPH0234738A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| JPH02194142A (en) * | 1989-01-21 | 1990-07-31 | Kobe Steel Ltd | Al-base alloy powder for sintering |
| JPH0525575A (en) * | 1990-11-19 | 1993-02-02 | Inco Alloys Internatl Inc | High temperature aluminum alloy |
| JPH05239583A (en) * | 1992-02-28 | 1993-09-17 | Yoshida Kogyo Kk <Ykk> | High strength heat resistant aluminum alloy, its compacted and caked material and its production |
| JP2006104563A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN ABRASION RESISTANCE AND WORKABILITY |
| JP2006104562A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY |
| WO2006040938A1 (en) * | 2004-10-08 | 2006-04-20 | Kabushiki Kaisha Kobe Seiko Sho | HEAT RESISTANT Al BASE ALLOY EXCELLING IN HIGH-TEMPERATURE FATIGUE PROPERTY, DUMPING PROPERTY, ABRASION RESISTANCE AND WORKABILITY |
| JP2006104564A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY AND VIBRATION-DAMPING PROPERTY |
| JP2006104561A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY |
| JP2007039748A (en) * | 2005-08-03 | 2007-02-15 | Kobe Steel Ltd | HEAT RESISTANT Al-BASED ALLOY |
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0234740A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| JPH0234738A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| JPH02194142A (en) * | 1989-01-21 | 1990-07-31 | Kobe Steel Ltd | Al-base alloy powder for sintering |
| JPH0525575A (en) * | 1990-11-19 | 1993-02-02 | Inco Alloys Internatl Inc | High temperature aluminum alloy |
| JPH05239583A (en) * | 1992-02-28 | 1993-09-17 | Yoshida Kogyo Kk <Ykk> | High strength heat resistant aluminum alloy, its compacted and caked material and its production |
| JP2006104562A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY |
| JP2006104563A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN ABRASION RESISTANCE AND WORKABILITY |
| WO2006040938A1 (en) * | 2004-10-08 | 2006-04-20 | Kabushiki Kaisha Kobe Seiko Sho | HEAT RESISTANT Al BASE ALLOY EXCELLING IN HIGH-TEMPERATURE FATIGUE PROPERTY, DUMPING PROPERTY, ABRASION RESISTANCE AND WORKABILITY |
| JP2006104564A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY AND VIBRATION-DAMPING PROPERTY |
| JP2006104561A (en) * | 2004-10-08 | 2006-04-20 | Kobe Steel Ltd | HEAT-RESISTANT Al-BASED ALLOY SUPERIOR IN HIGH-TEMPERATURE FATIGUE PROPERTY |
| JP4704722B2 (en) * | 2004-10-08 | 2011-06-22 | 株式会社神戸製鋼所 | Heat-resistant Al-based alloy with excellent wear resistance and workability |
| JP4704720B2 (en) * | 2004-10-08 | 2011-06-22 | 株式会社神戸製鋼所 | Heat-resistant Al-based alloy with excellent high-temperature fatigue properties |
| JP2007039748A (en) * | 2005-08-03 | 2007-02-15 | Kobe Steel Ltd | HEAT RESISTANT Al-BASED ALLOY |
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