JPH0372002A - Alloy steel powder for parts having high strength, high toughness and high accuracy and manufacture of sintered alloy steel using this - Google Patents
Alloy steel powder for parts having high strength, high toughness and high accuracy and manufacture of sintered alloy steel using thisInfo
- Publication number
- JPH0372002A JPH0372002A JP1205623A JP20562389A JPH0372002A JP H0372002 A JPH0372002 A JP H0372002A JP 1205623 A JP1205623 A JP 1205623A JP 20562389 A JP20562389 A JP 20562389A JP H0372002 A JPH0372002 A JP H0372002A
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- Prior art keywords
- alloy steel
- powder
- weight
- steel powder
- toughness
- 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.)
- Granted
Links
- 239000000843 powder Substances 0.000 title claims abstract description 39
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000010791 quenching Methods 0.000 claims abstract description 12
- 230000000171 quenching effect Effects 0.000 claims abstract description 12
- 238000011282 treatment Methods 0.000 claims abstract description 12
- 238000005496 tempering Methods 0.000 claims abstract description 8
- 239000011230 binding agent Substances 0.000 claims abstract description 7
- 239000000314 lubricant Substances 0.000 claims abstract description 6
- 238000005245 sintering Methods 0.000 claims abstract description 5
- 239000002245 particle Substances 0.000 claims abstract description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- 229910000967 As alloy Inorganic materials 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 abstract description 21
- 239000010959 steel Substances 0.000 abstract description 21
- 238000010438 heat treatment Methods 0.000 abstract description 18
- 229910052759 nickel Inorganic materials 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract 2
- 238000009740 moulding (composite fabrication) Methods 0.000 abstract 2
- 238000000137 annealing Methods 0.000 abstract 1
- 239000006185 dispersion Substances 0.000 abstract 1
- 230000005496 eutectics Effects 0.000 abstract 1
- 238000003754 machining Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 abstract 1
- 239000002131 composite material Substances 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 7
- 230000008859 change Effects 0.000 description 7
- 238000005275 alloying Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 238000004663 powder metallurgy Methods 0.000 description 5
- 238000005204 segregation Methods 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000011812 mixed powder Substances 0.000 description 4
- JKQOBWVOAYFWKG-UHFFFAOYSA-N molybdenum trioxide Inorganic materials O=[Mo](=O)=O JKQOBWVOAYFWKG-UHFFFAOYSA-N 0.000 description 4
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 4
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 3
- 238000000576 coating method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 239000010439 graphite Substances 0.000 description 3
- 229910002804 graphite Inorganic materials 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000002265 prevention Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- LNAZSHAWQACDHT-XIYTZBAFSA-N (2r,3r,4s,5r,6s)-4,5-dimethoxy-2-(methoxymethyl)-3-[(2s,3r,4s,5r,6r)-3,4,5-trimethoxy-6-(methoxymethyl)oxan-2-yl]oxy-6-[(2r,3r,4s,5r,6r)-4,5,6-trimethoxy-2-(methoxymethyl)oxan-3-yl]oxyoxane Chemical compound CO[C@@H]1[C@@H](OC)[C@H](OC)[C@@H](COC)O[C@H]1O[C@H]1[C@H](OC)[C@@H](OC)[C@H](O[C@H]2[C@@H]([C@@H](OC)[C@H](OC)O[C@@H]2COC)OC)O[C@@H]1COC LNAZSHAWQACDHT-XIYTZBAFSA-N 0.000 description 1
- WRIDQFICGBMAFQ-UHFFFAOYSA-N (E)-8-Octadecenoic acid Natural products CCCCCCCCCC=CCCCCCCC(O)=O WRIDQFICGBMAFQ-UHFFFAOYSA-N 0.000 description 1
- LQJBNNIYVWPHFW-UHFFFAOYSA-N 20:1omega9c fatty acid Natural products CCCCCCCCCCC=CCCCCCCCC(O)=O LQJBNNIYVWPHFW-UHFFFAOYSA-N 0.000 description 1
- QSBYPNXLFMSGKH-UHFFFAOYSA-N 9-Heptadecensaeure Natural products CCCCCCCC=CCCCCCCCC(O)=O QSBYPNXLFMSGKH-UHFFFAOYSA-N 0.000 description 1
- 239000001856 Ethyl cellulose Substances 0.000 description 1
- ZZSNKZQZMQGXPY-UHFFFAOYSA-N Ethyl cellulose Chemical compound CCOCC1OC(OC)C(OCC)C(OCC)C1OC1C(O)C(O)C(OC)C(CO)O1 ZZSNKZQZMQGXPY-UHFFFAOYSA-N 0.000 description 1
- ZQPPMHVWECSIRJ-UHFFFAOYSA-N Oleic acid Natural products CCCCCCCCC=CCCCCCCCC(O)=O ZQPPMHVWECSIRJ-UHFFFAOYSA-N 0.000 description 1
- 239000005642 Oleic acid Substances 0.000 description 1
- XTXRWKRVRITETP-UHFFFAOYSA-N Vinyl acetate Chemical compound CC(=O)OC=C XTXRWKRVRITETP-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 239000001913 cellulose Substances 0.000 description 1
- 229920002678 cellulose Polymers 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 235000019325 ethyl cellulose Nutrition 0.000 description 1
- 229920001249 ethyl cellulose Polymers 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- QXJSBBXBKPUZAA-UHFFFAOYSA-N isooleic acid Natural products CCCCCCCC=CCCCCCCCCC(O)=O QXJSBBXBKPUZAA-UHFFFAOYSA-N 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229920000609 methyl cellulose Polymers 0.000 description 1
- 239000001923 methylcellulose Substances 0.000 description 1
- 235000010981 methylcellulose Nutrition 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- ZQPPMHVWECSIRJ-KTKRTIGZSA-N oleic acid Chemical compound CCCCCCCC\C=C/CCCCCCCC(O)=O ZQPPMHVWECSIRJ-KTKRTIGZSA-N 0.000 description 1
- 239000005011 phenolic resin Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 239000000344 soap Substances 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
- 229920001187 thermosetting polymer Polymers 0.000 description 1
- 239000004416 thermosoftening plastic Substances 0.000 description 1
- 238000009692 water atomization Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
[産業上の111用分野1
本発明は、鉄系粉末冶金技術の分野に属し、高強度、高
靭性、高精度部品用の合金鋼粉、およびこの合金鋼粉を
用いて熱処理時の寸法変化のばらつきの少ない焼結部品
を製造するための方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field 1] The present invention belongs to the field of iron-based powder metallurgy technology, and relates to an alloy steel powder for high strength, high toughness, and high precision parts, and a method for producing this alloy steel powder. The present invention relates to a method for manufacturing sintered parts with less variation in dimensional change during heat treatment using the present invention.
〔従来の技術J
近年、粉末冶金技術は大幅に進歩し、輸送機器、産業機
器への焼結部品の適用が進んできた。[Conventional Technology J] Powder metallurgy technology has advanced significantly in recent years, and sintered parts have been increasingly applied to transportation equipment and industrial equipment.
自動車用ギア等は、それらの中でも高強度、高靭性、高
精度が要求される部品である。これらの部品を粉末冶金
によって製造する場合、高強度化を図るために合金元素
を添加し、さらに熱処理を侑す必要がある。Automotive gears and the like are parts that require high strength, high toughness, and high precision. When these parts are manufactured by powder metallurgy, it is necessary to add alloying elements and further heat treatment in order to increase the strength.
特開昭62−146203に述べられているように、合
金焼結体に熱処理を施すことが試みられているが引張強
さはたかだか120kgf/mrn”であり、それ以上
の高強度の要求には対処できな(/X。As described in Japanese Patent Application Laid-Open No. 62-146203, attempts have been made to heat treat the alloy sintered body, but the tensile strength is only 120 kgf/mrn", and higher strength is not required. I can't deal with it (/X.
また、特開昭61−231102においてはNi、Mo
を増加させ、また結合剤によってFe扮に合金元素及び
Cを結合させ、高圧縮性を保ち高強度を狙うことが試み
られているが、この場合ち引張り強さは晟大でも120
kgf/mrn″である。また、Ni、Moなどの合金
成分の添加はマルテンサイト変態(Ms)点を低下させ
る作用があり、焼入れ、焼戻し等の熱処理を施した際に
オーステナイトを生成させ、寸法変化のばらつきを引き
起こす可能性がある。In addition, in JP-A-61-231102, Ni, Mo
Attempts have been made to increase the alloying element and C using a binder to maintain high compressibility and high strength, but in this case, the tensile strength is 120
kgf/mrn''.Additionally, the addition of alloy components such as Ni and Mo has the effect of lowering the martensitic transformation (Ms) point, and when heat treatment such as quenching and tempering is performed, austenite is generated and the dimensions are This may cause variation in changes.
[発明が解決しようとする課題1
本発明者らは焼結体の高強度、高靭性を達成するための
複合合金粉末及びその製造方法をさきに提示した(特願
昭63−137400)。[Problem to be Solved by the Invention 1] The present inventors have previously proposed a composite alloy powder and a method for producing the same for achieving high strength and high toughness of a sintered body (Japanese Patent Application No. 137400/1982).
この方法においては、Nilの低減に伴い、焼結体中の
オーステナイトの生成を抑制し、高強度、高靭性を達成
している。一方、高強度化のために、浸炭焼入れを施し
た場合、過浸炭によって寸法精度がばらつく問題がある
。In this method, with the reduction of Nil, the formation of austenite in the sintered body is suppressed, and high strength and high toughness are achieved. On the other hand, when carburizing and quenching is performed to increase strength, there is a problem that dimensional accuracy varies due to overcarburizing.
本発明はこれにさらに熱処理時の寸法精度を向上させる
改善を加え、高強度、高靭性かつ熱処理時の寸法精度が
すぐれた
■ 焼結体用合金鋼粉、及び
■ 焼結合金鋼の製造方法
を与えるものである。The present invention further improves the dimensional accuracy during heat treatment, and provides (1) an alloy steel powder for sintered bodies with high strength, high toughness, and excellent dimensional accuracy during heat treatment, and (2) a method for producing sintered alloy steel. It gives
[課題を解決するための手段] 本発明者らは焼結体の高強度化、高靭性化。[Means to solve the problem] The present inventors have attempted to improve the strength and toughness of a sintered body.
高精度化について研究した結果、以下のことを見出し本
発明を完成した。つまり、
(1)Ni:0.5〜3.5重量%、
Mo:0.7〜3.5重量%、
C:0.3〜0.8虫酸%、
残部Feに合金鋼粉の化学組成を限定し、(2)m粉に
潤滑剤とバインダーとの共溶融物により黒鉛粉を付着さ
せ、焼結体中のC偏析を抑制し、
(3)焼入れ、焼戻し処理を施すこと
で高強度、高靭性、かつ熱処理時の寸法変化のばらつき
の少ない焼結合金鋼が得られることがわかった。As a result of research into high precision, the following findings were made and the present invention was completed. In other words, (1) Chemical composition of alloyed steel powder: Ni: 0.5-3.5% by weight, Mo: 0.7-3.5% by weight, C: 0.3-0.8% insectic acid, balance Fe. (2) Attach graphite powder to M powder using a co-melt of lubricant and binder to suppress C segregation in the sintered body, (3) High strength by quenching and tempering. It was found that a sintered alloy steel with high toughness and little variation in dimensional change during heat treatment can be obtained.
化学組成を上記(1)のように限定することによって、
強度低下および熱処理時の寸法変化のばらつきの要因と
なるオーステナイトが焼結体中に多量に発生するのを防
ぐ。By limiting the chemical composition as described in (1) above,
This prevents a large amount of austenite from forming in the sintered body, which causes a decrease in strength and variation in dimensional changes during heat treatment.
また、焼結体中のCの偏析は、焼入れ時における焼結体
中の不均一な変態を生じせしめ、寸法変化のばらつきを
増大させるので、黒鉛粉を銅粉に付着することによって
、焼結体中のC偏析を抑制する。In addition, the segregation of C in the sintered body causes non-uniform transformation in the sintered body during quenching, increasing the variation in dimensional changes. Suppresses C segregation in the body.
さらに焼入れ、焼戻し処理は、焼結体の強靭化に必要で
ある。Furthermore, quenching and tempering treatments are necessary to toughen the sintered body.
[作用]
本発明の成分、及び熱処理条件等の限定理由は以下の通
りである。合金成分の含有量は機械的特性上の要求から
決定される。[Operation] The reasons for limiting the components, heat treatment conditions, etc. of the present invention are as follows. The content of alloy components is determined based on requirements for mechanical properties.
Nilは0.5〜3.5重量%とする。強度及び靭[生
の向上の効果を得るためには0.5重量%以上の添加が
必要である。一方、3.5i量%を越えると焼結体中に
オーステナイトが過剰に生成する。Nil is set at 0.5 to 3.5% by weight. In order to obtain the effect of improving strength and toughness, it is necessary to add 0.5% by weight or more. On the other hand, if the content exceeds 3.5i, excessive austenite will be produced in the sintered body.
オーステナイトの過剰生成は熱処理時の寸法変化のばら
つきを増大し、また強度低下を招く。Excessive production of austenite increases the variation in dimensional changes during heat treatment and also causes a decrease in strength.
Mo量は0.7〜3.5重量%とする。Niと同様に高
強度と高靭性を達成させるために0.7重量%以上は必
要であり、3.5重置%を越えると、逆に焼結体の靭性
を阻害する。The amount of Mo is 0.7 to 3.5% by weight. Like Ni, 0.7% by weight or more is required to achieve high strength and toughness, and if it exceeds 3.5%, the toughness of the sintered body is adversely affected.
C看は、0.3〜0.8重量%とする。0.3重量%未
満では焼結体の強度向上に寄与しない。また0、8重量
%を越えると著しく靭性を阻害する。The content of C is 0.3 to 0.8% by weight. If it is less than 0.3% by weight, it does not contribute to improving the strength of the sintered body. Moreover, if it exceeds 0.8% by weight, toughness will be significantly impaired.
Ni、Moの添加方法については溶湯段階で合金化する
予合金法、または鉄粉にNi、MoFL子を拡散接合す
る複合合金法のどちらでち製造可能である。Regarding the method of adding Ni and Mo, production can be performed by either a pre-alloying method in which alloying is performed at the molten metal stage, or a composite alloying method in which Ni and MoFL particles are diffusion bonded to iron powder.
次に、上記の鋼粉に黒鉛粉を付着させる方法について述
べる。潤滑剤はステアリン酸亜鉛などの金属石鹸等通常
の粉末冶金に用いられるものでよく、バインダは、例え
ば酢酸ビニル、エチルセルロース、メチルセルロース、
フェノール樹脂など熱可塑性のもので6よく、セルロー
ス誘導体系、熱硬化型などいずれでもよい、この潤滑剤
とバインダーを上記鋼粉と黒鉛粉と同時又は段階的に均
−になるまで十分に混合する。均一に混合した状態で9
0℃〜150℃に加熱して潤滑剤とバインダーの共溶融
物を生成し、黒鉛粉を銅粉に固着する。加熱温度は90
℃以下では付着力が不足する。しかし、加熱温度を15
0℃以上にしても付着力の向上はない。Next, a method for attaching graphite powder to the above-mentioned steel powder will be described. The lubricant may be one commonly used in powder metallurgy, such as metal soaps such as zinc stearate, and the binder may be, for example, vinyl acetate, ethyl cellulose, methyl cellulose,
The lubricant and binder, which may be thermoplastic such as phenol resin, cellulose derivative, thermosetting, etc., are thoroughly mixed with the steel powder and graphite powder at the same time or in stages until they are homogeneous. . 9 in a uniformly mixed state
Heating to 0°C to 150°C creates a co-melt of lubricant and binder, which fixes the graphite powder to the copper powder. Heating temperature is 90
Adhesion is insufficient below ℃. However, the heating temperature is 15
There is no improvement in adhesion even at temperatures above 0°C.
粉末の成形は通常の粉末冶金と同様に成形圧力4〜Lo
t/cm″で行う、成形、焼結の回数は1回以上何回で
もよいが高密度とすることにより一層の高強度、高靭性
が得られる。Powder molding is performed at a molding pressure of 4 to Lo, as in normal powder metallurgy.
The number of times of molding and sintering performed at t/cm'' may be one or more times, but higher strength and toughness can be obtained by increasing the density.
本発明では、また上記焼結体に焼入れ、焼戻し処理を施
すことが必須である。焼入れ処理とは、鋼を所定温度に
加熱し、急冷する処理を示し、焼戻し処理とは、鋼を所
定温度に加熱し空冷あるいは徐冷する処理を示す、焼入
れ温度は加熱時に均一なオーステナイト組織とするため
800℃以上が望ましく、また950℃を越えるとオー
ステナイトが粗大化し靭性が低下するため950℃を上
限温度とする。In the present invention, it is also essential to subject the sintered body to quenching and tempering treatments. Quenching treatment refers to a treatment in which steel is heated to a predetermined temperature and then rapidly cooled. Tempering treatment refers to a treatment in which steel is heated to a predetermined temperature and then air cooled or slowly cooled. The quenching temperature is a process in which a uniform austenite structure is formed during heating. Therefore, the temperature is desirably 800°C or higher.If the temperature exceeds 950°C, the austenite becomes coarse and the toughness decreases, so the upper limit temperature is set at 950°C.
焼戻し温度は100℃未満では靭性が低く、250℃よ
り高いと、強度が低下するため。If the tempering temperature is less than 100°C, the toughness will be low, and if it is higher than 250°C, the strength will be reduced.
100〜250℃が好ましい。100-250°C is preferred.
[実施例1
実施例1
一80メツシュの水アトマイズFe扮に一325メツシ
ュのカーボニルNi粉と三酸化Mo (Mo03)とを
所定の割合で混合し、水素ガス雰囲気中にて、875℃
で60分焼鈍し、解砕して、Ni:1.76i量%、M
o:1.0Offi量%の複合合金鋼粉を得た。[Example 1 Example 1 180 mesh water atomized Fe, 1325 mesh carbonyl Ni powder and Mo trioxide (Mo03) were mixed at a predetermined ratio, and the mixture was heated at 875°C in a hydrogen gas atmosphere.
Annealed for 60 minutes, crushed, Ni: 1.76i amount%, M
A composite alloy steel powder containing o: 1.0 Offi amount % was obtained.
上記′鋼粉に黒鉛粉0.6重量%、ステアリン酸亜鉛1
.0重、量%、オレイン酸0.2重置%を混合し、温度
120℃で10分撹拌して、黒鉛粉を鋼粉表面に固着し
た。Above 'steel powder, graphite powder 0.6% by weight, zinc stearate 1
.. 0% by weight and 0.2% by weight of oleic acid were mixed and stirred at a temperature of 120° C. for 10 minutes to fix graphite powder on the surface of the steel powder.
次に上記鋼粉を超硬金型を用い、7t、/cm’の圧力
で成型し、75%H2−25%N2ガス(乾)雰囲気中
で850℃、30分焼結した後、7t/crn”の圧力
で再圧縮した。Next, the above steel powder was molded using a cemented carbide mold at a pressure of 7t/cm', and sintered at 850°C for 30 minutes in a 75%H2-25%N2 gas (dry) atmosphere. It was recompressed at a pressure of "crn".
さらに75%H2−25%N2ガス(乾)雰囲気中で1
250℃、60分再焼結を行い、得られた焼結体に85
0℃で60分加熱後60℃の油中へ焼入れ、次に180
℃の油中で60分保持して焼戻しを施し、引張試験、シ
ャルピー衝撃試験を行った。Furthermore, 1 in a 75% H2-25% N2 gas (dry) atmosphere.
Re-sintering was performed at 250°C for 60 minutes, and the resulting sintered body had a
After heating at 0℃ for 60 minutes, quenching in oil at 60℃, then 180℃
It was tempered by holding it in oil at ℃ for 60 minutes, and then subjected to a tensile test and a Charpy impact test.
また、外径60mm、内径25mm、高さ5、5 m
mのリングを10枚成形し、各工程毎に、各リングにつ
いて互いに直角的な2方向で外径(X、Y)を測定し、
その各工程での変化の差(△X−△Y)の絶対値の標準
偏差を求め1寸法精度を評価した。第1表に、引張試験
、シャルピー衝撃値、焼結体密度、熱処理前後での寸法
精度を示す。In addition, the outer diameter is 60 mm, the inner diameter is 25 mm, and the height is 5.5 m.
10 m rings were molded, and at each step, the outer diameter (X, Y) of each ring was measured in two directions perpendicular to each other.
The standard deviation of the absolute value of the difference in change (ΔX−ΔY) in each step was determined and the one-dimensional accuracy was evaluated. Table 1 shows the tensile test, Charpy impact value, sintered body density, and dimensional accuracy before and after heat treatment.
また同表中には本実施例と同じ複合鋼粉を用い、黒鉛粉
0.6重量%、ステアリン酸亜鉛1.0重量%を混扮し
1本実施例と同じ条件で実験した結果を比較例として示
す。In addition, the same table shows the results of an experiment conducted under the same conditions as in this example using the same composite steel powder as in this example, mixed with 0.6% by weight of graphite powder and 1.0% by weight of zinc stearate, as a comparative example. Shown as
双方とも引張強度、シャルピー衝撃値、焼結体密度には
明らかな差は認められないが、寸法精度がCを偏析防正
したものは0.012%であるか、単純混粉すると、0
.025%となり、Cを偏析防止処理することによって
寸法変化のばらつきがほぼ2分の1になる。There is no obvious difference in tensile strength, Charpy impact value, or sintered compact density between the two, but the dimensional accuracy of C with segregation prevention is 0.012%, or when simply mixed powder is 0.012%.
.. 025%, and by applying segregation prevention treatment to C, the variation in dimensional change is reduced to approximately 1/2.
実施例2
一80メツシュの水アトマイズFe扮に一325メツシ
ュのカーボニルNi扮の添加量を変え、MoO3扮を一
定看混合し、実施例1と同じ方法でNi:0.31〜5
.lO重機知の複合合金鋼粉を得た。Example 2 The addition amount of 180 mesh water atomized Fe layer and 1325 mesh carbonyl Ni layer was changed, MoO3 layer was mixed for a certain period, and Ni: 0.31 to 5 was added in the same manner as in Example 1.
.. A composite alloy steel powder of lO heavy duty was obtained.
これらの鋼粉に黒鉛粉0.6重置%を実施例1と同じ方
法で固着し、その後に実応例1と同じ方法で熱処理焼結
体を製造し、引張強さ、シャルピー衝撃値、焼結体密度
、寸法精度を1l11定した。結果を第2表に示す。0.6% of graphite powder was fixed to these steel powders in the same manner as in Example 1, and then a heat-treated sintered body was produced in the same manner as in Example 1, and the tensile strength, Charpy impact value, The density and dimensional accuracy of the sintered body were set at 1l11. The results are shown in Table 2.
Ni:0.31i量%のものは寸法変化のばらつきは少
ないが、強度、靭性が低い。The one containing 0.31i% Ni has little variation in dimensional change, but has low strength and toughness.
また、Nlが3.82重量%以上のものは強度も多少低
くなり、寸法精度は顕著に低下することがわかる。Furthermore, it can be seen that when the Nl content is 3.82% by weight or more, the strength is somewhat lowered and the dimensional accuracy is significantly lowered.
実施例3 ここでは添加するC量の影響を示す。Example 3 Here, the influence of the amount of C added is shown.
実施例1と同じ複合合金鋼粉に黒鉛粉0.3重量%、0
.6重量%、0.9重量%をそれぞれ実施例11と同じ
方法で固着した鋼粉と、黒鉛粉0.2重徽%、0.4重
遣%、0.6重量%、0.9重置%にステアリン酸亜鉛
1.0重量%を単純混粉した鋼粉を製造した。The same composite alloy steel powder as in Example 1 was added with 0.3% by weight of graphite powder.
.. 6% by weight and 0.9% by weight of steel powder fixed in the same manner as in Example 11, and graphite powder of 0.2% by weight, 0.4% by weight, 0.6% by weight, and 0.9% by weight. A steel powder was produced by simply mixing 1.0% by weight of zinc stearate.
これらの鋼粉を用い、実施例1と同じ方法で焼結体を製
造し、熱処理を施し、引張強度、シャルピー衝撃値、焼
結体密度1寸法精度を測定した。Using these steel powders, sintered bodies were produced in the same manner as in Example 1, subjected to heat treatment, and measured for tensile strength, Charpy impact value, sintered body density, and 1-dimensional accuracy.
結果を第3表に示す。The results are shown in Table 3.
黒鉛添加量が0.3重置%、0.6重置%の場合。When the amount of graphite added is 0.3% and 0.6%.
寸法変化のばらつきは単純混粉に比べて偏析防止の処理
したもののほうが顕著に小さい。The variation in dimensional changes is significantly smaller in the segregation-prevention treatment than in the simple mixed powder.
黒鉛添加量が0.9重置%の場合でも同様なことがわか
るが、強度、靭性ともに急激に低下している。また、0
.2重量%では強度が低い。Similar results can be seen when the amount of graphite added is 0.9% by weight, but both the strength and toughness decrease rapidly. Also, 0
.. At 2% by weight, the strength is low.
実施例4 ここでは添加するMo量の影響を示す。Example 4 Here, the influence of the amount of Mo added will be shown.
−80メツシユの水アトマイズFe扮に=325メツシ
ュのカーボニルNi扮を一定量とMOO3扮を添加量を
変えて混合し、実施例1と同じ方法でNi:1.76重
量%、Mo:0.50重量%〜4.50重量%の複合合
金鋼粉を得た。-80 meshes of water atomized Fe coatings were mixed with a certain amount of =325 meshes of carbonyl Ni coatings and MOO3 coatings in varying amounts, and the same method as in Example 1 was carried out, with Ni: 1.76% by weight, Mo: 0. Composite alloy steel powder containing 50% to 4.50% by weight was obtained.
これらの鋼粉に対して実施例2と同じ方法で黒鉛を添加
し、引張強度、シャルピー衝撃値、焼結体密度1寸法変
化のばらつきを測定した。結果を第4表に示す、Moが
0.5重量%のものは引張強さが142.2 k g
f/mrw?と本請求範囲内の6のに比べて著しく低い
、またMOが3.5重量%を越えるものについては、シ
ャルピー衝撃値が著しく低く、靭性の急激な低下が見ら
れる。また寸法精度も急激に低下している。Graphite was added to these steel powders in the same manner as in Example 2, and the tensile strength, Charpy impact value, and variation in 1 dimensional change in sintered body density were measured. The results are shown in Table 4. The tensile strength of the one containing 0.5% by weight of Mo was 142.2 kg.
f/mrw? If the MO content exceeds 3.5% by weight, the Charpy impact value is extremely low, and a sharp decrease in toughness is observed. Moreover, the dimensional accuracy has also decreased rapidly.
実施例5 水アトマイズによって、Ni:1.94重量%。Example 5 Ni: 1.94% by weight by water atomization.
Mo:1.05重量%の予合金鋼粉を製造し、水素ガス
雰囲気中で還元処理を行った後、−80メツシユで分級
して上記組成の予合金鋼粉を得た。Pre-alloyed steel powder containing Mo: 1.05% by weight was produced, subjected to reduction treatment in a hydrogen gas atmosphere, and then classified using a -80 mesh to obtain pre-alloyed steel powder having the above composition.
上記鋼粉について、実施例1と同様の実験を行い、単純
混合粉と黒鉛固着粉の諸特性を測定した。第5表に結果
を示す。Regarding the above steel powder, experiments similar to those in Example 1 were conducted to measure various properties of the simple mixed powder and the graphite-fixed powder. Table 5 shows the results.
予合金鋼粉においても寸法精度のばらつきが単純混粉で
は0.022%だが、黒鉛固着扮では0.0IQ%とな
り、複合合金鋼粉と同様の効果が得られた。For the pre-alloyed steel powder, the variation in dimensional accuracy was 0.022% for the simple mixed powder, but it was 0.0IQ% for the graphite-fixed powder, and the same effect as the composite alloyed steel powder was obtained.
[発明のく力東]
以にの結果により、本発明は極めて高い強度と靭性を徨
成し、かつ熱処理峙の寸法変化のばらつきが少ない焼結
合金鋼を与えるものであり、高強度、I’;;靭性、高
精度が要求される自動ili用a!械部品々とにff用
である。[The Power of the Invention] Based on the results described above, the present invention provides a sintered alloy steel that has extremely high strength and toughness, and has little variation in dimensional change during heat treatment, and has high strength and I. ';;A for automatic iris that requires toughness and high precision! It is for ff on mechanical parts.
11願人 川崎製鉄株式会社 代 理 人 弁理り 小 十三 住 lフ11 applicants Kawasaki Steel Co., Ltd. teenager Reason Man excuse small Thirteen residence lf
Claims (1)
前記Cが黒鉛粉の形で銅粉粒子表面に潤滑剤とバインダ
ーとの共溶融物により固着されていることを特徴とする
高強度、高靭性、高精度部品用合金鋼粉。 2 第1項記載の合金鋼粉を用い、1回以上の成形及び
1回以上の焼結を施すことにより焼結合金鋼を製造し、
さらにこの焼結合金鋼に焼入れ、焼き戻し処理を施すこ
とを特徴とする高強度、高靭性、高精度部品用焼結合金
鋼の製造方法。[Claims] 1. As alloy components: Ni: 0.5% to 3.5% by weight Mo: 0.7% to 3.5% by weight C: 0.3% to 0.8% by weight An alloy steel powder containing % by weight or less, the remainder being substantially Fe,
An alloy steel powder for use in high-strength, high-toughness, and high-precision parts, characterized in that the C is fixed to the surface of copper powder particles in the form of graphite powder by a co-melt of a lubricant and a binder. 2. Using the alloy steel powder described in paragraph 1, producing a sintered alloy steel by performing one or more forming operations and one or more sintering operations,
A method for producing a sintered alloy steel for high strength, high toughness, and high precision parts, which further comprises subjecting the sintered alloy steel to quenching and tempering treatments.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1205623A JP2606928B2 (en) | 1989-08-10 | 1989-08-10 | High-strength, high-toughness, high-precision alloy steel powder for parts and method for producing sintered alloy steel using the same |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1205623A JP2606928B2 (en) | 1989-08-10 | 1989-08-10 | High-strength, high-toughness, high-precision alloy steel powder for parts and method for producing sintered alloy steel using the same |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH0372002A true JPH0372002A (en) | 1991-03-27 |
JP2606928B2 JP2606928B2 (en) | 1997-05-07 |
Family
ID=16509952
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Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1205623A Expired - Fee Related JP2606928B2 (en) | 1989-08-10 | 1989-08-10 | High-strength, high-toughness, high-precision alloy steel powder for parts and method for producing sintered alloy steel using the same |
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6227308A (en) * | 1985-07-24 | 1987-02-05 | Nippon Denso Co Ltd | Method and apparatus for producing ultrafine particle |
JP2014037870A (en) * | 2012-08-17 | 2014-02-27 | Ntn Corp | Electric linear actuator |
-
1989
- 1989-08-10 JP JP1205623A patent/JP2606928B2/en not_active Expired - Fee Related
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6227308A (en) * | 1985-07-24 | 1987-02-05 | Nippon Denso Co Ltd | Method and apparatus for producing ultrafine particle |
JP2014037870A (en) * | 2012-08-17 | 2014-02-27 | Ntn Corp | Electric linear actuator |
Also Published As
Publication number | Publication date |
---|---|
JP2606928B2 (en) | 1997-05-07 |
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