JPS58224163A - Wear-resistant sintered alloy and its manufacture - Google Patents
Wear-resistant sintered alloy and its manufactureInfo
- Publication number
- JPS58224163A JPS58224163A JP10670282A JP10670282A JPS58224163A JP S58224163 A JPS58224163 A JP S58224163A JP 10670282 A JP10670282 A JP 10670282A JP 10670282 A JP10670282 A JP 10670282A JP S58224163 A JPS58224163 A JP S58224163A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- alloy
- melting point
- low melting
- sintered body
- 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
Abstract
Description
【発明の詳細な説明】
〔発明の技術分野〕
本発明は耐摩耗性焼結合金とその製造方法に関し、更に
詳しくは、ロータリーコンプレッサ−のブレードに用い
て有効な耐摩耗性、耐焼付性、耐接触疲労性に優れた焼
結合金とその製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Technical Field of the Invention] The present invention relates to a wear-resistant sintered alloy and a method for manufacturing the same. This invention relates to a sintered alloy with excellent contact fatigue resistance and a method for producing the same.
例えばエアコンのロータリーコンプレッサーのブレード
は、通常鉄系の焼結合金で構成されていて、これはシャ
ツ）Ｋ装着されているローラの面と接触してシリンダ内
を冷媒ガスの吸込室と吐出室に２分割し、シャフトの回
転に伴ってシリンダの摺動面の間を往復運動する。その
とき、ブレードの摺動面には主に吐出圧と吸込圧の差圧
が反復して加わるために、ブレードの摺動面が摩耗し、
またシリンダの側の摺動面も摩耗する。For example, the blades of an air conditioner's rotary compressor are usually made of iron-based sintered alloy, which comes into contact with the surface of the roller that is attached to the cylinder and flows into the refrigerant gas suction and discharge chambers. It is divided into two parts and moves back and forth between the sliding surfaces of the cylinder as the shaft rotates. At that time, the sliding surface of the blade is worn out mainly because the pressure difference between the discharge pressure and the suction pressure is repeatedly applied to the sliding surface of the blade.
The sliding surface on the cylinder side also wears out.
更には、シリンダ内で生ずる液圧縮によって、シリンダ
とブレードの間に供給される潤滑油が流出し、その結果
、ブレードとシリンダが相互乃 の摺動面で焼付
き現象を起生じ易すくなる。Furthermore, due to the liquid compression that occurs within the cylinder, the lubricating oil supplied between the cylinder and the blade flows out, and as a result, the blade and cylinder tend to seize on their sliding surfaces.
ビ
そのため、ブレードの摺動面に表面硬化処理を施してそ
の耐摩耗性を高めることが行なわれている。Therefore, the sliding surface of the blade is subjected to surface hardening treatment to improve its wear resistance.
例えば、表面硬化処理のために従来から行なわれている
方法としては、焼結合金の外表面に浸炭若し、〈は浸炭
窒化層を形成する方法（特公昭５０−４４４７号参照）
又は銅若しくは銅合金を含浸した焼結金属製品に加炭法
、炭窒化法を適用して表面硬化する方法（＠公昭５３−
２３７６１号参照）がある。For example, a conventional method for surface hardening treatment is to form a carburized or carbonitrided layer on the outer surface of a sintered alloy (see Japanese Patent Publication No. 4447/1983).
Or a method of surface hardening by applying carburization method or carbonitriding method to sintered metal products impregnated with copper or copper alloy (@ Kosho 53-
23761)).
このうち、ブレード表面に耐摩耗性の窒化層、すなわち
、審化物の硬質粒子の集合層を形成する場合、効果が充
分に発揮されるだめには、ブレードの表面、すなわちシ
リンダとの摺動面に分散する硬質粒子がブレードを構成
する焼結合金の基体に強固に保持されていて脱落しない
ととが必要である。Among these, when forming a wear-resistant nitrided layer on the blade surface, that is, a layer of aggregated hard particles of abrasive material, in order for the effect to be fully exhibited, the surface of the blade, that is, the sliding surface with the cylinder, must be formed. It is necessary that the hard particles dispersed in the blade be firmly held by the sintered alloy base that constitutes the blade so that they do not fall off.
しかしながら、この場合、一般に硬質粒子はそれ自体脆
弱であり、基体との結合性も悪いので基体から脱落し易
すく、脱落し差場合にはか １えってその脱落粒
子がブレードとシリンタ′の摺動面でアブレーション、
ラッピング作用を起して、ブレード及びシリンダの摩耗
を一層促進するという問題が発生する。However, in this case, the hard particles are generally fragile themselves and have poor bonding properties with the base, so they easily fall off from the base. Ablation on the moving surface,
A problem arises in that a lapping effect occurs, further accelerating wear of the blade and cylinder.
本発明は、高面圧下で、潤滑条件の悪いところで使用し
ても、優れた耐摩耗性、耐焼付性、耐接触疲労性を備え
た新規な組成の焼結合金とその製造方法の桿供を目的と
する。The present invention provides a sintered alloy with a novel composition that has excellent wear resistance, seizure resistance, and contact fatigue resistance even when used under high surface pressure and in poor lubrication conditions, and a method for producing the same. With the goal.
本発明の耐摩耗性焼結合金は、表面が窒化層から成り、
炭素０．２〜０．４重ｉ％、ケイ素０．２〜０．５重量
％、マンガン０．５〜１．０重量％、ニッケル３，０〜
４．０重量％、クロム１．０〜２，０重量％、モリブデ
ン０．２〜０．４重量％、チタン２．５〜３．０重量％
、アルミニウム０．７〜１．２重量％、残部が鉄である
多孔質焼結体と、該焼結体に溶浸された低融点金属若し
くは低融点合金のいずれか又は両方との複合体であるこ
とを特徴とし、その製造方法は、炭素０．２〜０．４重
量％、ケイ素０．２〜０．５重量％、マンガン０．５〜
１．０重量％、ニッケル３０〜４．０重量％、クロム１
．０〜２．０重量、チ、モリブデン０．２〜０．４重量
％、チタン２５〜３．０重量％、アルミニウム０．７〜
１．２型針チ、残部が鉄である組成の粉末を、加圧成形
して成形体とし；該成形体を焼結して多孔質の焼結体と
し；得られた焼結体を窒化処理して表面に窒化層を形成
し；ついで、該焼結体に１低融点金属又は低融点合金を
溶浸することを特徴とする。The wear-resistant sintered alloy of the present invention has a nitride layer on its surface,
Carbon 0.2-0.4% by weight, Silicon 0.2-0.5% by weight, Manganese 0.5-1.0% by weight, Nickel 3.0-
4.0% by weight, chromium 1.0-2.0% by weight, molybdenum 0.2-0.4% by weight, titanium 2.5-3.0% by weight
, a composite of a porous sintered body containing 0.7 to 1.2% by weight of aluminum, the balance being iron, and either or both of a low melting point metal or a low melting point alloy infiltrated into the sintered body. The manufacturing method is characterized by the following: carbon 0.2-0.4% by weight, silicon 0.2-0.5% by weight, manganese 0.5-0.
1.0% by weight, nickel 30-4.0% by weight, chromium 1
．． 0 to 2.0 weight%, molybdenum 0.2 to 0.4 weight%, titanium 25 to 3.0 weight%, aluminum 0.7 to
1. A powder having a composition of a type 2 needle and the balance being iron is press-molded to form a compact; the compact is sintered to form a porous sintered body; the obtained sintered body is nitrided. It is characterized in that it is treated to form a nitrided layer on the surface; and then the sintered body is infiltrated with a low melting point metal or a low melting point alloy.
本発明の焼結合金は、表面に窒化層が形成されていする
多孔質の焼結体と、該焼結体の空孔部分に溶浸された低
融点金属又は低融点合金との複合体である。The sintered alloy of the present invention is a composite of a porous sintered body having a nitride layer formed on the surface and a low melting point metal or low melting point alloy infiltrated into the pores of the sintered body. be.
この焼結合金は次のようにして製造される。This sintered alloy is manufactured as follows.
まず、上記した成分組成の粉末を用意する。First, a powder having the above-described component composition is prepared.
使用する粉末は、各成分単独の粉末を所定割合いで混合
した混合粉又は各成分の任意な組合せによって調製した
合金粉のいずれであってもよいが、混合時の偏析、組織
むらを防ぐ意味からして、予め調製された各成分の所定
割合いの合金粉を用いることが、耐摩耗性の点からは好
ましい。The powder used may be either a mixed powder made by mixing individual powders of each component at a predetermined ratio, or an alloy powder prepared by any combination of each component, but in order to prevent segregation and uneven structure during mixing, From the viewpoint of wear resistance, it is preferable to use an alloy powder containing predetermined proportions of each component prepared in advance.
各成分の組成の限定理由は以下のとおシである。炭素（
Ｃ）が龜２重量−未満の場合には、得らｉｌ、た焼結合
金の充分な硬さが得られず、また０、４重量％を超すと
その靭性が低下して脆くなる。ケイ素（Ｓｔ）が０．２
重ｆ！＃、チ未満の場合には、得られた焼結合金の焼も
どし軟化抵抗が減少し、０．５重量％を超えてもその効
果はそれ以上大きくならない。マンガン（Ｍｎ）は、焼
結合金の焼入れ性を著しく改善する成分で、ニッケル（
Ｎｉ）、クロム（Ｃｒ）、モリブデン（ＭＯ）との共存
下ではその効果は顕著であるが、ｏ、５〜１．０重ｉチ
の範囲から外れると、効果は充分に発揮されない。The reasons for limiting the composition of each component are as follows. carbon(
If C) is less than 2% by weight, the resulting sintered alloy will not have sufficient hardness, and if it exceeds 0.4% by weight, its toughness will decrease and it will become brittle. Silicon (St) is 0.2
Heavy f! When the content is less than # and 1, the tempering softening resistance of the obtained sintered alloy decreases, and even when it exceeds 0.5% by weight, the effect does not become any greater. Manganese (Mn) is a component that significantly improves the hardenability of sintered alloys.
The effect is remarkable in the coexistence with Ni), chromium (Cr), and molybdenum (MO), but the effect is not sufficiently exhibited when the content is outside the range of 5 to 1.0 weight i.
ニッケル（Ｎｉ ）が３．０重量−未満の場合には、得
られた合金の芯部での靭性低下、焼入れ性の減少を招き
、また４、０ＭＭ１％を超えてもそれら特性の向上は認
められない。クロムＣＣｒ）は、窒化、４ 層の形成
の厚みを大きくする成分で、１．０重量％未満の場合に
け、充分な硬さと厚みの窒化層を形成するのに多大の処
理時間を要し、また、２、 Ｏ、重量チを超えてもそれ
以上の効果は認められない。モリブデン（ＭＯ）は、窒
化処理時に発生する焼もとし脆性を軽減する機能を果す
成分であるが、０．２〜０．４重蒙］％の範囲から外れ
るとその機能は充分に発揮されない。チタン（Ｔｉ ）
は、その量が多いほど窒化層の形成速度が大とたりまた
形成された窒化層の硬度は高くなるが、その効果は２．
５重量−以上から充分に表われる。If the nickel (Ni) content is less than 3.0% by weight, the resulting alloy will have a decrease in toughness and hardenability in the core, and even if it exceeds 4.0MM1%, no improvement in these properties will be observed. I can't do it. Chromium (CCr) is a component that increases the thickness of the nitrided layer, and if it is less than 1.0% by weight, it takes a lot of processing time to form a nitrided layer with sufficient hardness and thickness. Moreover, even if the weight exceeds 2, O, no further effect is observed. Molybdenum (MO) is a component that functions to reduce the temper embrittlement that occurs during nitriding treatment, but if it is out of the range of 0.2 to 0.4% by weight, its function will not be fully exhibited. Titanium (Ti)
The larger the amount, the faster the formation rate of the nitride layer and the harder the formed nitride layer, but the effect is 2.
It is fully visible from 5 weight or more.
しかし、３．０重′Ｉｔチを超えるとフェライト組織と
なってしまい窒化層の機械的強度の低下をもたらす６最
後に、アルミニウム（Ａ））は窒化層の硬度向上に寄与
する成分であり、それは０．７重量％以上で充分に発揮
される。しかし、１．２重−３１チを超えると、Ｔｌと
同様匠窒化層にフェライト組織が発達してその機械的強
度の低下、更には窒化層の厚みの減少をもたらす。鉄は
バランス成分である。However, if it exceeds 3.0%, it becomes a ferritic structure, resulting in a decrease in the mechanical strength of the nitrided layer.6Finally, aluminum (A)) is a component that contributes to improving the hardness of the nitrided layer. It is fully exhibited at 0.7% by weight or more. However, if the thickness exceeds 1.2 times - 31 times, a ferrite structure develops in the nitrided layer, similar to Tl, resulting in a decrease in its mechanical strength and further a decrease in the thickness of the nitrided layer. Iron is a balance component.
用する粉末の粒径は格別限定されないが、後述する気孔
率及び機械的強度との関係からして５〜８０μｍの範囲
にあることが好ましい。Although the particle size of the powder used is not particularly limited, it is preferably in the range of 5 to 80 μm in view of the relationship with the porosity and mechanical strength described below.
さて、以上のような組成の粉末を、所定の型の中に充填
したのち加圧成形して成形体とする。Now, the powder having the composition as described above is filled into a predetermined mold and then pressure-molded to form a molded body.
このときの加圧条件は焼結体の気孔率との関係で重要で
あり、圧力が４〜７ ｔｏｎ／ｌｙｎ”の範囲にあるこ
とが好オしい。圧力が４ ｔｏｎ／ＣＷｔより小さい場
合には得られた焼結体の気孔率は大きくなるが、逆にそ
の機械的強度が低下する。また７ｔＯｒＶｃ：を超える
と機械的強度の向上は達成されるが、気孔率は小さくな
り後述する溶浸工程にとって不都合である。The pressurizing conditions at this time are important in relation to the porosity of the sintered body, and it is preferable that the pressure be in the range of 4 to 7 ton/lyn.If the pressure is less than 4 ton/CWt, The porosity of the obtained sintered body increases, but its mechanical strength decreases.If it exceeds 7tOrVc, an improvement in mechanical strength is achieved, but the porosity decreases and the porosity decreases as described below. This is inconvenient for the soaking process.
得られた成形体は、そのまま、焼結される。The obtained molded body is sintered as it is.
このときの焼結条件は、成形条件と同様に気孔率、機械
的強度に影響を与え、例えば焼結温度は１１００〜１２
００ ｔｌ；の範囲にあることが好ましい。The sintering conditions at this time affect the porosity and mechanical strength in the same way as the molding conditions; for example, the sintering temperature is 1100 to 12
It is preferably in the range of 00 tl;
１１００Ｃ未満のときは気孔重大、強度小の焼結体とな
り、逆に１２０（１’を超えると気孔率小、強度大の焼
結体となってしまう、、また、焼結時の雰囲気は、焼結
体の酸化防止という点からして例えはアンモニア分解ガ
ス雰囲気であることが好ましい。焼結時間は格別限定さ
れないが、通常、３０〜６０分間である。If the temperature is less than 1100C, the sintered body will have significant porosity and low strength, while if it exceeds 120 (1'), the sintered body will have low porosity and high strength.Also, the atmosphere during sintering is From the viewpoint of preventing oxidation of the sintered body, an ammonia decomposition gas atmosphere is preferable.The sintering time is not particularly limited, but is usually 30 to 60 minutes.
このようにして得られた焼結体にとって気孔率は重要で
、本発明の場合には、５〜３０％の範囲に設定されるこ
とが好ましい。５％未満の場合には、後述する溶浸処理
が円滑に進行せず、また３０％を超えると機械的強度が
低下して例えばブレードとしての使用に耐え得ない。こ
の気孔率の腑整は、前述したとおり、成形条件、焼結条
件を適宜組合せて行なわれる。The porosity is important for the sintered body thus obtained, and in the case of the present invention, it is preferably set in the range of 5 to 30%. If it is less than 5%, the infiltration treatment described below will not proceed smoothly, and if it exceeds 30%, the mechanical strength will decrease and it will not be possible to use it as a blade, for example. This adjustment of the porosity is carried out by appropriately combining the molding conditions and sintering conditions, as described above.
つぎに、焼結体の窒化処理が行なわれ、該焼結体の表面
部分を窒化層にする。窒化処理は、常用される気体法、
イオン法、液体法などいずれの方法でも行なうことがで
きるが、液体法の場合には、窒化処理に用いる各種の溶
融塩が焼結体の気孔内に浸透してしまいその除去が困難
になるので好ｔ Ｌ、 ＜なく、通常、気体法、イオン
法が適用される。Next, the sintered body is subjected to nitriding treatment to form a nitrided layer on the surface of the sintered body. Nitriding treatment is carried out by the commonly used gas method,
This can be done using either the ion method or the liquid method, but in the case of the liquid method, the various molten salts used for nitriding penetrate into the pores of the sintered body, making it difficult to remove them. Preferably, a gas method or an ion method is usually applied.
このように表面部分に窒化層が形成された焼結体は次に
低融点金属若しくは低融点合金を該焼結体の空孔部分に
溶浸して本発明の焼結合金になる。The sintered body with the nitrided layer formed on the surface thereof is then infiltrated into the pores of the sintered body with a low melting point metal or a low melting point alloy to obtain the sintered alloy of the present invention.
用いる低融点金属としては、融点が低く軟質で、耐焼付
性に優れかつ浸透性の良好な本のであれば伺であっても
よいが、具体的には、鉛。The low melting point metal to be used may be lead, as long as it has a low melting point, is soft, has excellent seizure resistance, and good permeability, but specifically lead.
銅、スズ、インジウムなどが好ましい。また、これら金
属を単体で用いてもよいが、更に、これら金属の任意の
組合せによる合金を用いることもできる。Copper, tin, indium, etc. are preferred. Furthermore, although these metals may be used alone, alloys of any combination of these metals may also be used.
溶浸の方法としては、上記した金属若しくは合金の溶融
液に焼結体を浸漬する方法、密閉容器中に焼結体を収納
し、そこに溶融金属若しくは合金を加圧含浸する方法、
又は焼結体の表面に上記金属若しくは合金の板又は線を
載置し全体を金属若しくは合金の融点以上に加熱する方
法などをあげることができる。Infiltration methods include a method of immersing the sintered body in a molten liquid of the metal or alloy described above, a method of storing the sintered body in a closed container and impregnating the molten metal or alloy therein under pressure,
Alternatively, a method may be used in which a plate or wire of the metal or alloy is placed on the surface of the sintered body and the entire body is heated to a temperature higher than the melting point of the metal or alloy.
１ ００・３５重ｆＪ−チ・ＳｉＯ，４重量
％・”°０°８重量％ 、 Ｎｉ ３．５重量％ 、
Ｃｒ １．４重量−Ｉ ＭＯ０，３重量％ 、 Ｔｉ
２．８重量＠ 、ｈノ１．０ＭＮ％ 、残部がＦｅであ
る組成の合金粉（平均粒径３０μｍ）を型の巾に所定倍
充填し ５ ｔｏｎ／ｃｍ２の圧力で成形した。得られ
た成形体をアンモニア分解ガス中で１１．０（Ｉ’、３
０分間焼結した。気孔率１−５チの焼結体が得られた。100・35 weight fJ-chi・SiO, 4% by weight・”°0°8% by weight, Ni 3.5% by weight,
Cr 1.4wt-I MO0.3wt%, Ti
An alloy powder having a composition of 2.8 weight @ 1.0 MN%, the balance being Fe (average particle size 30 μm) was filled in the width of the mold to a predetermined ratio and molded at a pressure of 5 ton/cm 2 . The obtained molded body was heated to 11.0 (I', 3
Sintered for 0 minutes. A sintered body with a porosity of 1-5 was obtained.
この焼結体を、アンモニアガス中で６００ ｔＺ’ 。This sintered body was heated to 600 tZ' in ammonia gas.
３時間窒化処理した。その表面には深さ０．２ｍの窒化
層が形成さハ５、その硬さはＩ（ｖｌｌｏＯであった。Nitriding treatment was performed for 3 hours. A nitride layer with a depth of 0.2 m was formed on its surface, and its hardness was I(vlloO).
ついで、とれをＩ Ｘ １０−”ｐｏｒｒの真空中で、
Ｐｂ浴（温度５００ｔ：’ ）中に浸漬して溶浸処理を
施した。Then, the pieces were placed in a vacuum of I x 10-”porr.
Infiltration treatment was performed by immersing it in a Pb bath (temperature: 500 t:').
得られた焼結合金をアノ、スラー摩耗試験機にかけその
摩耗試験を行なった。試験条件は、相手相ＳＫ４、荷重
１０ｋｇ、速度１．２１気であった。摩耗Ｍ （ｍｙ
）と摩擦距離（Ｋｍ ）との関係を図（曲線Ａ）に示し
た。なお、比較のために、溶浸処理を施さない場合の結
果（曲線Ｂ）も図に併記した。The obtained sintered alloy was subjected to an abrasion test using a slurry abrasion tester. The test conditions were: opponent phase SK4, load 10 kg, and speed 1.21 Ki. Wear M (my
) and the friction distance (Km) is shown in the figure (curve A). For comparison, the results obtained without infiltration treatment (curve B) are also shown in the figure.
結果から明らかなように、本発明の焼結合金１窒化層か
らの硬質粒子の脱落による摩耗もなく、高面圧下で潤滑
条件の悪いところでも耐摩耗性、耐焼付性及び耐接触疲
労性に優り、ている。As is clear from the results, the sintered alloy 1 of the present invention does not suffer from wear due to shedding of hard particles from the nitrided layer, and has excellent wear resistance, seizure resistance, and contact fatigue resistance even under high surface pressure and poor lubrication conditions. It's better, it's better.
図は、焼結合金のアムスラー試験による摩耗量と摩擦距
離との関係曲線で、曲線Ａは本発明の焼結合金、曲線Ｂ
は溶浸処理を施さない場合を表わす。
席澤青献 （ｋｍ）−The figure shows the relationship curve between wear amount and friction distance by Amsler test of sintered alloy. Curve A is the sintered alloy of the present invention, curve B
represents the case without infiltration treatment. Seishen Takazawa (km) -
Claims (1)
％、ケイ素０．２〜０．５重量％、マンガン０、５〜１
．０重量−１＝ ツ）１ ル３．０〜４．０重量％、ク
ロム１．０〜２．０重量％、モリブデン０、２〜０．４
重量％、ｆ ＩＩ ｙ ２．５〜３． Ｏｆ量チ、アル
ミニウム０．７〜１．２重量％、残部が鉄である多孔質
焼結体と、該焼結体に溶浸された低融点金属若しくは低
融点合金のいずれが又は両方との複合体である仁とを特
徴とする耐摩耗性焼結合金。 ２、該低融点金属が鉛、銅、スズ、インジウムのいずれ
かであり、該低融点合金が該低融点金属の任意の組合せ
による合金である特許請求の範囲第１項記載の耐摩耗性
焼結合金。 ３、 炭素０．２〜０．４重量％、ケイ素０．２〜０．
５重量％、マンガン０．５〜１．０重量％、ニッケル３
．０〜４．０重量％、クロム１．０〜２．０重量％、モ
リブデン０．２〜０．４ｆｆｉ−３ｔ％、チタン２．５
〜３．０重量％、アルミニウム０７〜１．２重ｉｉｓ、
残部が鉄である組成の粉末を、加圧成形して成形体とし
； 核酸形体を焼結して多孔質の焼結体とし；得られた焼結
体を窒化処理して表面に窒化層を形成し；ついで、 該焼結体に、低融点金属又は低融点合金を溶浸すること
を特徴とする耐摩耗性焼結合金の製造方法。 ４、該低融点金属が鉛、銅、スズ、インジウムのいずれ
かであり、該低融点合金が該低融点金属の任意の組合せ
による合金である特許請求の範囲第３項記載の耐摩耗性
焼結合金の製造方法。[Claims] 1. The surface is composed of a nitride layer, carbon 0.2-0.4% by weight, silicon 0.2-0.5% by weight, manganese 0.5-1
．． 0 weight - 1 = 1) 3.0 to 4.0 weight %, chromium 1.0 to 2.0 weight %, molybdenum 0, 2 to 0.4
Weight %, f II y 2.5-3. A porous sintered body having an amount of 0.7 to 1.2% by weight of aluminum, the balance being iron, and either or both of a low melting point metal or a low melting point alloy infiltrated into the sintered body. A wear-resistant sintered alloy characterized by a composite core. 2. The wear-resistant sintering material according to claim 1, wherein the low melting point metal is lead, copper, tin, or indium, and the low melting point alloy is an alloy of any combination of the low melting point metals. Combined gold. 3. Carbon 0.2-0.4% by weight, Silicon 0.2-0.
5% by weight, manganese 0.5-1.0% by weight, nickel 3
．． 0 to 4.0 wt%, chromium 1.0 to 2.0 wt%, molybdenum 0.2 to 0.4ffi-3t%, titanium 2.5
~3.0% by weight, aluminum 07~1.2wt IIS,
Powder with a composition in which the balance is iron is press-molded to form a molded body; the nucleic acid form is sintered to form a porous sintered body; the obtained sintered body is nitrided to form a nitrided layer on the surface. and then infiltrating the sintered body with a low melting point metal or a low melting point alloy. 4. The wear-resistant sintering material according to claim 3, wherein the low melting point metal is any one of lead, copper, tin, and indium, and the low melting point alloy is an alloy of any combination of the low melting point metals. Manufacturing method of bonded metal.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10670282A JPS58224163A (en) | 1982-06-23 | 1982-06-23 | Wear-resistant sintered alloy and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10670282A JPS58224163A (en) | 1982-06-23 | 1982-06-23 | Wear-resistant sintered alloy and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS58224163A true JPS58224163A (en) | 1983-12-26 |
Family
ID=14440329
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10670282A Pending JPS58224163A (en) | 1982-06-23 | 1982-06-23 | Wear-resistant sintered alloy and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS58224163A (en) |
-
1982
- 1982-06-23 JP JP10670282A patent/JPS58224163A/en active Pending
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