JPH05263181A - Manufacture of fe base sintered alloy member having high strength and high toughness - Google Patents
Manufacture of fe base sintered alloy member having high strength and high toughnessInfo
- Publication number
- JPH05263181A JPH05263181A JP9355192A JP9355192A JPH05263181A JP H05263181 A JPH05263181 A JP H05263181A JP 9355192 A JP9355192 A JP 9355192A JP 9355192 A JP9355192 A JP 9355192A JP H05263181 A JPH05263181 A JP H05263181A
- Authority
- JP
- Japan
- Prior art keywords
- sintered alloy
- sintering
- alloy member
- powder
- high strength
- 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.)
- Withdrawn
Links
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、高強度および高靭性
を有するＦｅ基焼結合金部材の製造法に関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an Fe-based sintered alloy member having high strength and high toughness.
【０００２】[0002]
【従来の技術】従来、一般に、圧粉体を焼結して焼結体
とし、この焼結体に熱間鍛造加工を施した後、真空焼入
れまたは光輝焼入れと焼戻しの熱処理を施すことにより
Ｆｅ基焼結合金部材を製造する方法が知られており、ま
たこの方法が各種歯車やコネクティングロッドなどの機
械構造部材の製造に適用されていることも良く知られて
いる。2. Description of the Related Art Conventionally, in general, a green compact is sintered into a sintered body, which is hot-forged, and then vacuum-quenched or bright-quenched and heat-treated to obtain Fe. A method for producing a base sintered alloy member is known, and it is also well known that this method is applied to the production of mechanical structural members such as various gears and connecting rods.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の各種機械
装置の高性能化および多機能化に伴ない、これの構造部
材には薄肉化および小型化が強く要求されているが、上
記の従来方法によって製造されたＦｅ基焼結合金部材は
強度および靭性不足が原因で、これに十分満足に対応す
ることができないのが現状である。On the other hand, with the recent progress in performance and multifunction of various mechanical devices, there is a strong demand for the structural members thereof to be thin and compact. Under the present circumstances, the Fe-based sintered alloy member manufactured by the method cannot sufficiently satisfy this because of insufficient strength and toughness.
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者等は、
上述のような観点から、上記の従来方法によって製造さ
れたＦｅ基焼結合金部材に比して、一段とすぐれた強度
と靭性を有するＦｅ基焼結合金部材を製造すべく研究を
行なった結果、上記の従来方法によるＦｅ基焼結合金部
材の製造においては、熱間鍛造加工後の焼結体は、熱間
鍛造加工前に存在していた気孔が消減して緻密化したも
のになっているが、前記気孔が存在していた部分の粉末
粒子間の結合は機械的結合になっているにすぎず、した
がってこれに再度焼結処理、すなわち圧粉体の焼結（以
下、１次焼結という）と同じ焼結機能を発揮する条件で
の焼結（以下、２次焼結という）を施すと、前記の機械
的結合する粉末粒子が相互に冶金的に結合するようにな
り、この焼結による冶金的結合は機械的結合に比して一
段と強固なものであるから、この結果としてＦｅ基焼結
合金部材の強度と靭性が著しく向上するようになるとい
う研究結果を得たのである。Therefore, the present inventors have
From the above viewpoints, as a result of conducting research to produce an Fe-based sintered alloy member having further excellent strength and toughness as compared with the Fe-based sintered alloy member produced by the conventional method, In the production of the Fe-based sintered alloy member by the above-mentioned conventional method, the sintered body after the hot forging is densified by eliminating the pores existing before the hot forging. However, the bond between the powder particles in the portion where the pores were present is only a mechanical bond, and therefore the sintering process is performed again, that is, sintering of the green compact (hereinafter referred to as primary sintering). When the sintering is performed under the condition of exhibiting the same sintering function (hereinafter referred to as secondary sintering), the powder particles that mechanically bond with each other become metallurgically bonded to each other. Metallurgical bonding by binding is much stronger than mechanical bonding. That since, at the strength and toughness of the Fe-based sintered alloy member as a result got finding that become significantly improved.
【０００５】この発明は、上記の研究結果にもとづいて
なされたものであって、圧粉体を焼結（１次焼結）して
焼結体とし、この焼結体に熱間鍛造加工を施した後、真
空焼入れまたは光輝焼入れと焼戻しの熱処理を施すこと
によりＦｅ基焼結合金部材を製造するに際して、上記熱
間鍛造加工後に、１次焼結温度を越えない温度で、再度
焼結処理（２次焼結）を施して強度と靭性の向上をはか
るＦｅ基焼結合金部材の製造法に特徴を有するものであ
る。The present invention has been made based on the above-mentioned research results. The green compact is sintered (primarily sintered) into a sintered body, and this sintered body is subjected to hot forging. After producing the Fe-based sintered alloy member by vacuum quenching or bright quenching and tempering heat treatment, after the hot forging, the sintering treatment is performed again at a temperature not exceeding the primary sintering temperature. It is characterized by a method for producing an Fe-based sintered alloy member which is subjected to (secondary sintering) to improve strength and toughness.
【０００６】なお、この発明の方法を実施するに際して
は、重量％で（以下％は重量％を示す）、（ａ） 炭素
粉末：０．２〜０．７％、Ｆｅ−０．１〜５％Ｎｉ−
０．１〜２％Ｍｏ合金粉末：残り、（ｂ） 炭素粉末：
０．２〜０．７％、Ｆｅ：０．１〜３％Ｃｕ−０．１〜
５％Ｎｉ−０．１〜２％Ｍｏ合金粉末：残り、（ｃ）
炭素粉末：０．２〜０．７％、Ｆｅ−０．１〜２％Ｍｎ
−０．１〜２％Ｃｒ−０．１〜２％Ｍｏ合金粉末：残
り、（ｄ） 炭素粉末：０．２〜０．７％、Ｆｅ粉末：
残り、（ｅ） 炭素粉末：０．２〜０．７％、Ｃｕ粉
末：０．１〜５％、Ｆｅ粉末：残り、（ｆ） 炭素粉
末：０．２〜０．７％、Ｎｉ粉末：０．１〜５％、Ｆｅ
粉末：残り、（ｇ） 炭素粉末：０．２〜０．７％、Ｃ
ｕ粉末：０．１〜５％、Ｎｉ粉末、Ｆｅ粉末：残り、上
記（ａ）〜（ｇ）のいずれかの配合組成を有する混合粉
末の圧粉体を用いるのが望ましい。In carrying out the method of the present invention, in weight% (hereinafter,% means weight%), (a) carbon powder: 0.2 to 0.7%, Fe-0.1 to 5 % Ni-
0.1-2% Mo alloy powder: rest, (b) carbon powder:
0.2-0.7%, Fe: 0.1-3% Cu-0.1
5% Ni-0.1-2% Mo alloy powder: rest, (c)
Carbon powder: 0.2-0.7%, Fe-0.1-2% Mn
-0.1-2% Cr-0.1-2% Mo alloy powder: The rest, (d) Carbon powder: 0.2-0.7%, Fe powder:
Remaining (e) Carbon powder: 0.2 to 0.7%, Cu powder: 0.1 to 5%, Fe powder: Remaining, (f) Carbon powder: 0.2 to 0.7%, Ni powder: 0.1-5%, Fe
Powder: the rest, (g) Carbon powder: 0.2-0.7%, C
u powder: 0.1 to 5%, Ni powder, Fe powder: the rest, and it is desirable to use a powder compact of a mixed powder having any one of the above-mentioned compositional compositions (a) to (g).
【０００７】また、同じく１次焼結は、非酸化性雰囲気
中、温度：１１００〜１３００℃に３０〜１２０分間保
持、同２次焼結は、非酸化性雰囲気中、温度：１０００
〜１１５０℃に２０〜６０分間保持の条件で行なうのが
望ましい。Similarly, the primary sintering is maintained at a temperature of 1100 to 1300 ° C. for 30 to 120 minutes in a non-oxidizing atmosphere, and the secondary sintering is performed in a non-oxidizing atmosphere at a temperature of 1000.
It is desirable to carry out the treatment at a temperature of ~ 1150 ° C for 20 to 60 minutes.
【０００８】さらに、熱間鍛造加工は、非酸化性雰囲気
中、温度：９００〜１１００℃、鍛造圧下率：５〜６０
％の条件で行なうのがよい。Further, hot forging is performed in a non-oxidizing atmosphere at a temperature of 900 to 1100 ° C. and a forging reduction rate of 5 to 60.
It is better to do it in% condition.
【０００９】また、熱処理は、５×１０-1〜１×１０-5
toorの真空中あるいは非酸化性雰囲気中、温度：８５０
〜９５０℃に０．５〜３時間保持後焼入れの真空焼入れ
あるいは光輝焼入れと、大気中あるいは油中、温度：１
５０〜５００℃に０．５〜２時間保持の条件での焼戻し
処理からなる。The heat treatment is 5 × 10 -1 to 1 × 10 -5
In toor vacuum or non-oxidizing atmosphere, temperature: 850
Vacuum quenching or bright quenching after holding at ~ 950 ° C for 0.5 to 3 hours and in air or oil, temperature: 1
It consists of tempering treatment under the condition of holding at 50 to 500 ° C. for 0.5 to 2 hours.
【００１０】[0010]
【実施例】つぎに、この発明の方法を実施例により具体
的に説明する。原料粉末として、それぞれ表１に示され
る成分組成を有し、かつアトマイズにより１００メッシ
ュ以下の粒度としたＦｅ基合金粉末、同じくアトマイズ
により１００メッシュ以下の粒度としたＦｅ粉末、Ｃｕ
粉末、およびＮｉ粉末、さらにカーボンブラックを用意
し、これら原料粉末を表１，２に示される配合組成に配
合し、これに１％のステアリン酸亜鉛を加えてＶ型ミキ
サーで混合した後、４〜８ton ／cm2 の範囲内の所定の
圧力でプレス成形して圧粉体Ａ〜Ｎを形成し、ついでこ
れら圧粉体を、Ｈ2 ガス雰囲気中、温度：７００℃に１
時間保持の条件で焙焼を施してステアリン酸亜鉛を除去
した後、表３，４に示される条件で１次焼結を行なって
同じく表３，４に示される理論密度比、並びに縦：１０
mm×横：１０mm×長さ：５５mmの寸法をもった焼結体と
し、これに表３，４に示される条件で熱間鍛造加工と２
次焼結を施し、引続いて表５，６に示される条件で真空
焼入れあるいは光輝焼入れと焼戻しの熱処理を施すこと
により本発明法１〜１４を実施し、それぞれＦｅ基焼結
合金部材を製造した。EXAMPLES Next, the method of the present invention will be specifically described by way of Examples. As a raw material powder, an Fe-based alloy powder having the composition of components shown in Table 1 and having a particle size of 100 mesh or less by atomization, an Fe powder having a particle size of 100 mesh or less by atomization, Cu
Powder, Ni powder, and carbon black were prepared, and these raw material powders were blended in the blending composition shown in Tables 1 and 2, and 1% zinc stearate was added thereto and mixed with a V-type mixer, and then 4 The green compacts A to N are formed by press molding at a predetermined pressure within the range of up to 8 ton / cm 2 , and these green compacts are then heated to 700 ° C. in a H 2 gas atmosphere at a temperature of 700 ° C.
After roasting under the conditions of holding time to remove zinc stearate, primary sintering was performed under the conditions shown in Tables 3 and 4, and theoretical density ratios also shown in Tables 3 and 4, and length: 10
mm x width: 10 mm x length: 55 mm, which is a sintered body, and hot forged under the conditions shown in Tables 3 and 4
The present invention methods 1 to 14 are carried out by subjecting to subsequent sintering, and subsequently to vacuum quenching or bright quenching and tempering heat treatment under the conditions shown in Tables 5 and 6 to produce Fe-based sintered alloy members, respectively. did.
【００１１】また、比較の目的で、２次焼結を行なわな
い以外は同一の条件で従来法１〜１４を行ない、Ｆｅ基
焼結合金部材を製造した。For the purpose of comparison, Fe-based sintered alloy members were manufactured by performing the conventional methods 1 to 14 under the same conditions except that secondary sintering was not performed.
【００１２】[0012]
【表１】 [Table 1]
【００１３】[0013]
【表２】 [Table 2]
【００１４】[0014]
【表３】 [Table 3]
【００１５】[0015]
【表４】 [Table 4]
【００１６】[0016]
【表５】 [Table 5]
【００１７】[0017]
【表６】 [Table 6]
【００１８】ついで、この結果得られた各種のＦｅ基焼
結合金部材について、強度および靭性を評価する目的
で、引張強さ、伸び、およびシャルピー値衝撃値（ＪＩ
Ｓ衝撃３号試験片、ノッチあり）を測定し、この結果を
表５，６に示した。Then, with respect to the various Fe-based sintered alloy members obtained as a result, tensile strength, elongation, and Charpy impact value (JI) were measured for the purpose of evaluating strength and toughness.
S impact No. 3 test piece with a notch) was measured, and the results are shown in Tables 5 and 6.
【００１９】表３〜６に示される結果から、本発明法１
〜１４で製造されたＦｅ基焼結合金部材は、いずれも２
次焼結のない従来法１〜１４によって製造されたＦｅ基
焼結合金部材１〜１４に比して高強度と高靭性を具備す
ることが明らかである。From the results shown in Tables 3 to 6, the method 1 of the present invention was used.
Fe-based sintered alloy members manufactured in any of
It is clear that it has high strength and high toughness as compared with the Fe-based sintered alloy members 1 to 14 produced by the conventional methods 1 to 14 without subsequent sintering.
【００２０】上述のように、この発明の方法によれば、
高強度および高靭性を有するＦｅ基焼結合金部材を製造
することができ、したがってこの結果のＦｅ基焼結合金
部材を適用すれば、これの薄肉化および小型化が可能と
なるばかりでなく、実用に際してすぐれた性能を著しく
長期に亘って発揮するようになるなど工業上有用な効果
がもたらされるのである。As mentioned above, according to the method of the present invention,
It is possible to manufacture an Fe-based sintered alloy member having high strength and high toughness. Therefore, if the resulting Fe-based sintered alloy member is applied, not only can it be made thinner and downsized, but also Industrially useful effects are brought about, such as excellent performance in practical use over a long period of time.
Claims (1)
体に熱間鍛造加工を施した後、真空焼入れまたは光輝焼
入れと焼戻しの熱処理を施すことによりＦｅ基焼結合金
部材を製造する方法において、 上記熱間鍛造加工後に、前記焼結温度を越えない温度
で、再度焼結処理を施すことを特徴とする高強度および
高靭性を有するＦｅ基焼結合金部材の製造法。1. A Fe-based sintered alloy obtained by sintering a green compact into a sintered body, subjecting this sintered body to hot forging, and then subjecting it to vacuum quenching or bright quenching and tempering heat treatment. In the method for manufacturing a member, after the hot forging process, a sintering treatment is performed again at a temperature not exceeding the sintering temperature, and a Fe-based sintered alloy member having high strength and high toughness is manufactured. Law.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9355192A JPH05263181A (en) | 1992-03-19 | 1992-03-19 | Manufacture of fe base sintered alloy member having high strength and high toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9355192A JPH05263181A (en) | 1992-03-19 | 1992-03-19 | Manufacture of fe base sintered alloy member having high strength and high toughness |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05263181A true JPH05263181A (en) | 1993-10-12 |
Family
ID=14085399
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9355192A Withdrawn JPH05263181A (en) | 1992-03-19 | 1992-03-19 | Manufacture of fe base sintered alloy member having high strength and high toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05263181A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015111338A1 (en) * | 2014-01-22 | 2015-07-30 | Ntn株式会社 | Sintered machine part and manufacturing method thereof |
| JP2015158002A (en) * | 2014-01-22 | 2015-09-03 | Ntn株式会社 | Sintered machine part and production method thereof |
| WO2015141807A1 (en) * | 2014-03-20 | 2015-09-24 | Ntn株式会社 | Bearing ring and roller bearing having said bearing ring |
| CN105899315A (en) * | 2014-01-22 | 2016-08-24 | Ntn株式会社 | Sintered machine part and manufacturing method thereof |
-
1992
- 1992-03-19 JP JP9355192A patent/JPH05263181A/en not_active Withdrawn
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015111338A1 (en) * | 2014-01-22 | 2015-07-30 | Ntn株式会社 | Sintered machine part and manufacturing method thereof |
| JP2015158002A (en) * | 2014-01-22 | 2015-09-03 | Ntn株式会社 | Sintered machine part and production method thereof |
| CN105899315A (en) * | 2014-01-22 | 2016-08-24 | Ntn株式会社 | Sintered machine part and manufacturing method thereof |
| US20160327144A1 (en) * | 2014-01-22 | 2016-11-10 | Ntn Corporation | Sintered machine part and manufacturing method thereof |
| WO2015141807A1 (en) * | 2014-03-20 | 2015-09-24 | Ntn株式会社 | Bearing ring and roller bearing having said bearing ring |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19990608 |