JP4140928B2 - Wear resistant hard sintered alloy - Google Patents
Wear resistant hard sintered alloy Download PDFInfo
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- JP4140928B2 JP4140928B2 JP29977396A JP29977396A JP4140928B2 JP 4140928 B2 JP4140928 B2 JP 4140928B2 JP 29977396 A JP29977396 A JP 29977396A JP 29977396 A JP29977396 A JP 29977396A JP 4140928 B2 JP4140928 B2 JP 4140928B2
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Description
【０００１】
【発明の属する技術分野】
本発明は、耐摩耗性，耐腐食性および低摩擦係数を有する硬質焼結合金に関し、具体的には、例えばノズル，メカニカルシール，軸受け部品，射出成形用金型，ボールペン用ボールなど耐摩耗性と共に、耐腐食性および潤滑性を必要とする用途に最適な耐摩耗性硬質焼結合金に関するものである。
【０００２】
【従来の技術】
粉末冶金製品のなかでも耐腐食性と耐摩耗性を兼備した硬質焼結合金として、ＷＣー（Ｃｏ−Ｃｒ）基超硬合金，ＷＣーＮｉ基超硬合金，ＷＣ−（Ｎｉ−Ｃｒ）基超硬合金が多用されている。近年、これら超硬合金の各種用途において、さらなる耐腐食性の向上や潤滑性付与による摩擦・摩耗の低減が求められている。
【０００３】
この問題を改善しようとして提案されている代表的なものに、特開昭５０−４５７０８号公報，特開昭５９−１３３３４６号公報，および特開昭６２−１１２７５０号公報がある。
【０００４】
【発明が解決しようとする課題】
耐摩耗性の改善に着目した先行技術の内、特開昭５０−４５７０８号公報には、Ｎｉ：６〜１２重量％とＣｒ：１〜４重量％とＭｏ：１〜４重量％と残り炭化タングステンでなるＷＣ−（Ｎｉ−Ｃｒ−Ｍｏ）基超硬合金が開示されている。同公報に開示の超硬合金は、耐腐食性は向上されているものの、摩擦・摩耗が余り改善さていなく満足できないという問題がある。
【０００５】
また、特開昭５９−１３３３４６号公報には、Ｗ：７５〜９５重量％，ＴｉとＴａまたはＴａの一部をＮｂに置換したもの０〜５重量％，カーボン：３〜８重量％の成分で、かつ結合相の鉄族金属：２〜２０重量％含有した焼結体組織中にＣｏ3Ｗ3Ｃを有せしめた超硬質焼結体について開示されている。同公報に開示されている超硬質焼結体は、組織中にＣｏ3Ｗ3Ｃを含有せしめることにより切削工具としての耐摩耗性が向上したというものであるが、耐腐食性の改善および強度と摩擦係数の低下については配慮されていないという問題がある。
【０００６】
さらに、特開昭６２−１１２７５０号公報には、炭化タングステンでなる分散相と、ＣｏにＮｉ，Ｃｒ，ＷおよびＣが固溶したＣｏ基合金でなる結合相からなる超硬合金製熱間圧延ロールについて開示されている。同公報に開示の超硬合金製熱間圧延ロールは、超耐熱合金でなるＣｏ基合金を結合相としていることから耐熱性にすぐれた超硬合金になっているのであるが、耐腐食性の改善、特に摩擦係数の低下については配慮されていないという問題がある。
【０００７】
本発明は、上記のような問題点を解決したもので、具体的には、超硬合金中にＣｏ3Ｗ3Ｃ，Ｎｉ2Ｗ4Ｃで代表される複合化合物の分散相を分散させ、かつ結合相中にＷを固溶させることにより、耐腐食性および耐摩耗性を大幅に向上させること、摩擦係数を低下させることが可能となった耐摩耗性硬質焼結合金の提供を目的とするものである。
【０００８】
【課題を解決するための手段】
本発明者らは、耐腐食性と耐摩耗性を兼備した硬質焼結合金について、長年に亘って検討していた所、超硬合金中にＣｏ3Ｗ3Ｃ，Ｎｉ2Ｗ4Ｃに代表される複合化合物を分散させると同時に、結合相中にＷを固溶させることにより、その目的が達成されるという知見を得て、本発明を完成するに至ったものである。
【０００９】
本発明の耐摩耗性硬質焼結合金は、Ｃｏおよび／またはＮｉとＷとを主成分として含む結合相：３〜１５重量％と、ＷとＣｏおよび／またはＮｉと炭素を含む複合化合物でなる分散相：５０重量％以下と、残りが炭化タングステンと不可避不純物からなることを特徴とするものである。
【００１０】
【発明の実施の形態】
本発明の耐摩耗性硬質焼結合金における結合相は、Ｃｏおよび／またはＮｉとＷを主成分とするもので、具体的には、例えばＣｏ−Ｗ合金，Ｎｉ−Ｗ合金，Ｃｏ−Ｎｉ−Ｗ合金，ＣｏーＷーＣｒ合金，Ｃｏ−Ｗ−Ｃｒ−Ｖ合金，Ｃｏ−Ｎｉ−Ｗ−Ｃｒ合金，Ｎｉ−Ｗ−Ｃｒ−Ｍｏ合金を挙げることができる。この結合相は、結合相に対してＣｏおよび／またはＮｉが７０重量％以上、Ｗが５〜３０重量％含有することが好ましく、さらにＣｏ，Ｎｉ，Ｗ以外の元素、例えばＣｒ，Ｖ，Ｍｏが含まれる場合には、１５重量％以下含有していると、耐腐食性および耐摩耗性が向上することから好ましいことである。この結合相量は、合金全体に対して３重量％未満になると、焼結が困難となって強度と硬さが低下し、逆に１５重量％を超え多くなると硬さ低下による耐摩耗性劣化が顕著となるために、３〜１５重量％と定めたものである。
【００１１】
本発明の耐摩耗性硬質焼結合金における分散相は、ＷとＣｏおよび／またはＮｉと炭素からなるＭ６Ｃ型複合化合物および／またはＭ12Ｃ型複合化合物でなり、具体的には、例えばＣｏ3Ｗ3Ｃ，Ｃｏ2Ｗ4Ｃ，Ｃｏ6Ｗ6Ｃ，Ｎｉ2Ｗ4Ｃおよびこれらの相互固溶体の中の１種以上からなる第１複合化合物でなる場合を挙げることができる。さらに、この複合化合物中のＷの一部もしくはＣｏおよび／またはＮｉの一部が周期律表の４ａ，５ａ，６ａ族元素に代表される他の元素により置換された複合化合物、具体的には、例えば（Ｃｏ，Ｃｒ）3Ｗ3Ｃ、（Ｎｉ，Ｃｒ，Ｍｏ）2Ｗ4Ｃ、（Ｃｏ，Ｃｒ）3（Ｗ，Ｍｏ）3Ｃの１種以上からなる第２複合化合物でなる場合を挙げることができる。この分散相は、焼結合金全体に対して５０重量％を超えて多くなると、強度低下と硬さ低下による耐摩耗性の劣化が顕著になる。分散相の特徴である潤滑性を、焼結合金として発揮させるために、焼結合金全体に対して５〜５０重量％含有していることが好ましいことである。
【００１２】
この分散相は、上述した第１複合化合物のみでなる場合、第２複合化合物のみでなる場合、または第１複合化合物と第２複合化合物の混在した場合でもよく、これらのうち、第１複合化合物の場合には、焼結合金全体に対して５〜４５重量％、第２複合化合物の場合には、焼結合金全体に対して５〜３０重量％含有していることが好ましいことである。このうち、第２複合化合物の場合は、ＷとＣｏおよび／またはＮｉとＣｒおよび／またはＭｏと炭素との複合化合物、具体的には、例えば（Ｃｏ，Ｃｒ）3Ｗ3Ｃ、Ｃｏ3（Ｗ，Ｃｒ）3Ｃ、（Ｃｏ，Ｎｉ）3（Ｗ，Ｍｏ）3Ｃ、（Ｎｉ，Ｍｏ）3Ｗ3Ｃ、（Ｎｉ，Ｃｒ，Ｍｏ）2Ｗ4Ｃでなる場合を挙げることができる。この第２複合化合物の場合におけるＣｒおよび／またはＭｏは、複合化合物全体に対して２０重量％以下固溶されている場合には、耐腐食性や耐摩耗性を向上させる効果が高いことから好ましい。
【００１３】
本発明の耐摩耗性硬質焼結合金は、上述したように実質的に結合相と分散相と炭化タングステンとでなる場合、または結合相と分散相と炭化タングステンの他に、さらに、周期律表の４ａ，５ａ，６ａ族元素の炭化物，窒化物およびこれらの相互固溶体の中の１種以上の立方晶結晶構造の化合物でなる硬質相が焼結合金全体に対して３０重量％以下含有している場合にも分散相と結合相の効果が充分に発揮され得ることから好ましいことである。この硬質相は、具体的には、例えば（Ｗ，Ｔｉ）Ｃ、（Ｗ，Ｔｉ）（ＣＮ）、ＴｉＮ、ＴｉＣ、Ｔｉ（ＣＮ）、Ｚｒ（ＣＮ）、（Ｗ，Ｔｉ，Ｔａ）Ｃ、（Ｗ，Ｔｉ，Ｔａ，Ｎｂ）Ｃ、ＴａＣ、ＮｂＮ、ＶＣなどを挙げることができる。硬質相は、組成成分によって、硬さ上昇による耐摩耗性の向上と炭化タングステン粒子の粒成長抑制と分散相の凝集防止による強度の改善効果を発揮し、その含有量が３０重量％を超え多くなると相対的に炭化タングステンの含有量が減少して強度・靱性が低下するため、３０重量％以下と定めたものである。
【００１４】
【作用】
本発明の耐摩耗性硬質焼結合金は、含有されたＣｏ3Ｗ3Ｃ，Ｎｉ2Ｗ4Ｃなどの分散相が潤滑性を付加して耐摩耗性を顕著に高める作用をし、Ｗを多量に固溶させた結合相が耐腐食性を改善する作用をしているものである。
【００１５】
【実施例】
まず、市販されている平均粒子径が０．５μｍのＷ，１．２μｍのＣｏ，０．０２μｍのカーボン（表中に「Ｃ」と記す），１．７μｍのＣｒ3Ｃ2，１．５μｍのＮｉ，の各粉末を用い、表１に示す配合組成に秤量し、ステンレス製ポットにアセトン溶媒と超硬合金製ボールと共に挿入して２４時間の混合粉砕後、乾燥して得た混合粉末をアルミナ製ルツボに挿入し、真空中で１２００℃×１時間の加熱処理を施して、表１に併記した複合化合物の混在した混合粉末ＡおよびＢを得た。このＡおよびＢの混合粉末のＸ線回折による組成，含有炭素量，平均粒子径を表１に併記した。
【００１６】
次に、上記Ｗ，Ｃｏ，Ｃ，Ｃｒ3Ｃ2，Ｎｉ，混合粉末ＡおよびＢ，市販されている平均粒子径が０．５μｍのＷＣ（表中に「ＷＣ／Ｆ」と記す），１．５μｍのＷＣ（表中に「ＷＣ／Ｍ」と記す），１．０μｍの（Ｗ，Ｔｉ）Ｃの複合炭化物（重量比でＷＣ／ＴｉＣ＝７０／３０），１．０μｍのＴａＣ，１．２μｍのＭｏの各粉末を用いて、表２に示す配合組成に秤量し、ステンレス製ポットにアセトン溶媒と超硬合金製ボールと共に挿入し、４８時間の混合粉砕後、乾燥して混合粉末を得た。これらの混合粉末を金型に充填し、２ｔｏｎ／ｃｍ2の圧力でもって約５．５×９．５×２９ｍｍの圧粉成形体を作製し、アルミナとカーボン繊維からなるシート上に設置し、雰囲気圧力１０Ｐａの真空中で、表２に併記した温度でもって１時間加熱保持して、本発明品１〜７および比較品１〜６の焼結合金を得た。
【００１７】
こうして得た焼結合金試料の１μｍダイヤモンドペーストによるラップ加工面をＸ線回折法により成分を同定した後、電子顕微鏡にて組織写真を撮り、画像処理装置にて、結合相と、Ｍ6ＣおよびＭ12Ｃ化合物である分散相と、硬質相と、ＷＣとの重量割合を求めて、その結果を表３に示した。さらに、Ｘ線マイクロアナライザーにより結合相中のＷ，Ｃｒの量を分析し、その結果を表３に併記した。一方、これらの試料を＃２３０のダイヤモンド砥石で湿式研削加工し、４．０×８．０×２５ｍｍの形状に作製し、ＪＩＳ規格による抗折力とＨＲＡ硬さを測定して、その結果を表４に示した。
【００１８】
次に、本発明品１〜７および比較品１〜６のラップ加工試料をＰＨ＝４．０の塩酸水溶液とＰＨ＝３．０の硝酸水溶液の中に常温で２４時間浸責した後、光学顕微鏡観察により腐食の有無を調査し、その結果を表４に併記した。この腐食試験における腐食程度の評価基準は、◎：全く腐食無し、○：僅かに腐食（やや曇り）、△：腐食有り（曇り）、×：著しい腐食（色調変化）で表示した。
【００１９】
また、本発明品１〜７および比較品１〜６と同一組成の混合粉末を用い、プレス成形，焼結，研削加工の工程を経て、φ３５×１０ｍｍの円板とφ５．６４×２０ｍｍの丸棒を製作した。これらをピンオンディスク型の摩擦試験機に同種材質の組合わせ（同一番号の試料の組合わせ）の円板と丸棒を着装し、水に２．０重量％のステアリン酸と５重量％のアルミナ粉（０．５μｍ）を添加した分散液中で、摩擦速度：１．０ｍ／ｓ，面圧：１．０ＭＰａ，摩擦時間：１０Ｈｒの条件で摩擦試験を実施した。この摩擦試験により得られた摩耗体積と摩擦係数の測定結果を表５に示した。
【００２０】
【表１】
【表２】
【表３】
【表４】
【表５】
【発明の効果】
本発明の耐摩耗性硬質焼結合金は、従来のＮｉ−Ｃｒ−Ｍｏ合金を結合相としたＷＣ基超硬合金およびＣｏ3Ｗ3Ｃの複合化合物を含有したＣｏ結合相でなるＷＣ基超硬合金に対比して、耐腐食性および耐摩耗性が顕著にすぐれており、かつ摩擦係数が低い傾向にあることから、耐摩耗性を必要とし、かつ腐食が進行しやすい用途、具体的には、例えば化学プラント，汚泥処理装置，湿式粉砕装置などに用いられる溶液，気体または粉末の混在した溶液を吹き付けるためのノズル、メカニカルシールとしての効果、さらには樹脂やインキによる耐摩耗性と耐腐食性を必要とする射出成形用金型，ボールペン用ボールなどとしての効果が期待されるものである。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a hard sintered alloy having wear resistance, corrosion resistance and a low coefficient of friction, and specifically, wear resistance such as nozzles, mechanical seals, bearing parts, injection molds, ballpoint pen balls, etc. In addition, the present invention relates to a wear-resistant hard sintered alloy that is optimal for applications that require corrosion resistance and lubricity.
[0002]
[Prior art]
Among powder metallurgy products, WC- (Co-Cr) -based cemented carbide, WC-Ni-based cemented carbide, WC- (Ni-Cr) -based as hard sintered alloys that have both corrosion resistance and wear resistance. Cemented carbide is often used. In recent years, in various applications of these cemented carbides, there has been a demand for further improvement of corrosion resistance and reduction of friction and wear by imparting lubricity.
[0003]
Representative examples proposed to improve this problem include Japanese Patent Laid-Open Nos. 50-45708, 59-133346, and 62-112750.
[0004]
[Problems to be solved by the invention]
Among the prior arts focused on improving the wear resistance, Japanese Patent Application Laid-Open No. 50-45708 discloses Ni: 6 to 12% by weight, Cr: 1 to 4% by weight, Mo: 1 to 4% by weight, and remaining carbonization. A WC- (Ni-Cr-Mo) based cemented carbide made of tungsten is disclosed. Although the cemented carbide disclosed in the publication has improved corrosion resistance, there is a problem that friction and wear are not improved so much and cannot be satisfied.
[0005]
JP-A-59-133346 discloses W: 75 to 95% by weight, Ti and Ta or a part of Ta substituted with Nb, 0 to 5% by weight, and carbon: 3 to 8% by weight. And an ultra-hard sintered body in which Co 3 W 3 C is contained in the sintered body structure containing 2-20% by weight of iron group metal in the binder phase. The ultra-hard sintered body disclosed in the publication is improved in wear resistance as a cutting tool by incorporating Co 3 W 3 C in the structure. There is a problem that the reduction of the friction coefficient is not considered.
[0006]
Further, JP-A-62-112750 discloses a cemented carbide hot rolling comprising a dispersed phase made of tungsten carbide and a bonded phase made of a Co-based alloy in which Ni, Cr, W and C are dissolved in Co. A roll is disclosed. The hot rolling roll made of cemented carbide disclosed in the publication is a cemented carbide having excellent heat resistance because it uses a Co-based alloy made of superheat resistant alloy as a binder phase. There is a problem that improvement is not taken into consideration, particularly about a decrease in the coefficient of friction.
[0007]
The present invention has solved the above-described problems. Specifically, a dispersed phase of a composite compound represented by Co 3 W 3 C and Ni 2 W 4 C is dispersed in a cemented carbide, The purpose of this invention is to provide a wear-resistant hard sintered alloy that can greatly improve corrosion resistance and wear resistance by reducing W in the binder phase, and can reduce the friction coefficient. To do.
[0008]
[Means for Solving the Problems]
The inventors of the present invention have been studying hard sintered alloys having both corrosion resistance and wear resistance for many years, and are represented by Co 3 W 3 C and Ni 2 W 4 C in cemented carbides. The present invention has been completed by obtaining the knowledge that the object is achieved by dispersing W in the binder phase and simultaneously dissolving W in the binder phase.
[0009]
The wear-resistant hard sintered alloy of the present invention comprises a composite phase containing 3 to 15% by weight of a binder phase containing Co and / or Ni and W as main components, and W and Co and / or Ni and carbon. Dispersed phase: 50% by weight or less, and the remainder consists of tungsten carbide and inevitable impurities.
[0010]
DETAILED DESCRIPTION OF THE INVENTION
The binder phase in the wear-resistant hard sintered alloy of the present invention is mainly composed of Co and / or Ni and W. Specifically, for example, a Co—W alloy, Ni—W alloy, Co—Ni— W alloy, Co-W-Cr alloy, Co-W-Cr-V alloy, Co-Ni-W-Cr alloy, Ni-W-Cr-Mo alloy can be mentioned. This binder phase preferably contains 70% by weight or more of Co and / or Ni and 5 to 30% by weight of W with respect to the binder phase, and further elements other than Co, Ni, W, such as Cr, V, Mo, etc. Is contained in an amount of 15% by weight or less, it is preferable because corrosion resistance and wear resistance are improved. When the amount of this binder phase is less than 3% by weight based on the whole alloy, sintering becomes difficult and the strength and hardness are reduced. Conversely, when it exceeds 15% by weight, the wear resistance is deteriorated due to the decrease in hardness. Is set to 3 to 15% by weight.
[0011]
Dispersed phase in the wear resistant hard sintered alloy of the present invention will become at M6C type complex compound and / or M 12 C type complex compound consisting of W and Co and / or Ni and carbon, specifically, for example, Co 3 W 3 C, Co 2 W 4 C, mention may be made of a case made of a Co 6 W 6 C, Ni 2 W 4 C , and the first complex compound consisting of one or more of these mutual solid solutions. Further, a composite compound in which a part of W or a part of Co and / or Ni in this composite compound is substituted with another element typified by Group 4a, 5a, 6a element of the periodic table, specifically For example, a case where the second composite compound is composed of at least one of (Co, Cr) 3 W 3 C, (Ni, Cr, Mo) 2 W 4 C, and (Co, Cr) 3 (W, Mo) 3 C Can be mentioned. When the amount of the dispersed phase exceeds 50% by weight with respect to the entire sintered alloy, the wear resistance is significantly deteriorated due to a decrease in strength and a decrease in hardness. In order to exhibit the lubricity characteristic of the dispersed phase as a sintered alloy, it is preferable to contain 5 to 50% by weight with respect to the entire sintered alloy.
[0012]
The dispersed phase may be composed of only the first composite compound, the second composite compound, or the first composite compound and the second composite compound. Of these, the first composite compound may be used. In this case, it is preferable to contain 5 to 45% by weight with respect to the whole sintered alloy, and in the case of the second composite compound, 5 to 30% by weight with respect to the whole sintered alloy. Among these, in the case of the second composite compound, a composite compound of W and Co and / or Ni and Cr and / or Mo and carbon, specifically, for example, (Co, Cr) 3 W 3 C, Co 3 ( Examples include W, Cr) 3 C, (Co, Ni) 3 (W, Mo) 3 C, (Ni, Mo) 3 W 3 C, and (Ni, Cr, Mo) 2 W 4 C. . Cr and / or Mo in the case of the second composite compound is preferable because it has a high effect of improving the corrosion resistance and wear resistance when 20% by weight or less is dissolved in the entire composite compound. .
[0013]
The wear-resistant hard sintered alloy of the present invention is substantially composed of a binder phase, a dispersed phase, and tungsten carbide as described above, or in addition to the binder phase, the dispersed phase, and tungsten carbide, in addition to the periodic table. 4a, 5a, and 6a element carbides, nitrides, and hard phases composed of one or more kinds of cubic crystal structure compounds among these solid solutions are contained in an amount of 30% by weight or less based on the entire sintered alloy. Even in such a case, the effects of the dispersed phase and the binder phase can be sufficiently exhibited, which is preferable. Specifically, this hard phase is, for example, (W, Ti) C, (W, Ti) (CN), TiN, TiC, Ti (CN), Zr (CN), (W, Ti, Ta) C, (W, Ti, Ta, Nb) C, TaC, NbN, VC and the like can be mentioned. Depending on the composition, the hard phase exhibits improved wear resistance due to increased hardness, improved grain strength of tungsten carbide particles, and improved strength by preventing aggregation of the dispersed phase, and its content exceeds 30% by weight. In this case, the content of tungsten carbide is relatively reduced and the strength and toughness are lowered. Therefore, the content is determined to be 30% by weight or less.
[0014]
[Action]
In the wear-resistant hard sintered alloy of the present invention, the dispersed phase such as Co 3 W 3 C, Ni 2 W 4 C and the like has an effect of remarkably enhancing wear resistance by adding lubricity. The binder phase that is dissolved in a large amount acts to improve the corrosion resistance.
[0015]
【Example】
First, commercially available W with an average particle size of 0.5 μm, Co with 1.2 μm, carbon with 0.02 μm (denoted as “C” in the table), 1.7 μm Cr 3 C 2 , 1.5 μm Each of the Ni powders was weighed to the composition shown in Table 1, inserted into a stainless steel pot with an acetone solvent and a cemented carbide ball, mixed and ground for 24 hours, and then dried to obtain a mixed powder. The mixture was inserted into an alumina crucible and subjected to heat treatment at 1200 ° C. for 1 hour in vacuum to obtain mixed powders A and B in which the composite compounds shown in Table 1 were mixed. Table 1 also shows the composition, carbon content, and average particle size of the mixed powder of A and B by X-ray diffraction.
[0016]
Next, W, Co, C, Cr 3 C 2 , Ni, mixed powders A and B, a commercially available WC having an average particle diameter of 0.5 μm (denoted as “WC / F” in the table), 1 0.5 μm WC (denoted as “WC / M” in the table), 1.0 μm (W, Ti) C composite carbide (WC / TiC = 70/30 by weight), 1.0 μm TaC, 1 Each powder of Mo of 2 μm was weighed into the composition shown in Table 2, inserted into a stainless steel pot with an acetone solvent and a cemented carbide ball, mixed and ground for 48 hours, dried and mixed powder Obtained. Filling the mold with these mixed powders, producing a compact of about 5.5 × 9.5 × 29 mm with a pressure of 2 ton / cm 2 , placing it on a sheet made of alumina and carbon fiber, In the vacuum of atmospheric pressure 10Pa, it heated and hold | maintained for 1 hour with the temperature written together in Table 2, and obtained the sintered alloy of this invention products 1-7 and the comparative products 1-6.
[0017]
After the components of the lapping surface of the sintered alloy sample thus obtained with 1 μm diamond paste were identified by X-ray diffraction, a structure photograph was taken with an electron microscope, and the binder phase, M 6 C and The weight ratio of the dispersed phase, which is the M 12 C compound, the hard phase, and WC was determined, and the results are shown in Table 3. Further, the amounts of W and Cr in the binder phase were analyzed by an X-ray microanalyzer, and the results are also shown in Table 3. On the other hand, these samples were wet-grinded with a # 230 diamond grindstone and fabricated into a 4.0 × 8.0 × 25 mm shape, and the bending strength and HRA hardness according to JIS standards were measured. It is shown in Table 4.
[0018]
Next, the lapped samples of the inventive products 1 to 7 and the comparative products 1 to 6 were immersed in a hydrochloric acid aqueous solution of PH = 4.0 and a nitric acid aqueous solution of PH = 3.0 at room temperature for 24 hours. The presence or absence of corrosion was examined by microscopic observation, and the results are also shown in Table 4. The evaluation criteria for the degree of corrosion in this corrosion test are indicated as follows: ◎: no corrosion, ◯: slight corrosion (slightly cloudy), △: corrosion (cloudy), ×: significant corrosion (color change).
[0019]
In addition, using mixed powders having the same composition as the inventive products 1 to 7 and comparative products 1 to 6, through a process of press molding, sintering and grinding, a φ35 × 10 mm disc and a φ5.64 × 20 mm round I made a stick. These are mounted on a pin-on-disk friction tester with discs and round bars of the same kind of material (combination of samples of the same number), and 2.0% by weight stearic acid and 5% by weight in water. A friction test was performed in a dispersion to which alumina powder (0.5 μm) was added under the conditions of friction speed: 1.0 m / s, surface pressure: 1.0 MPa, friction time: 10 Hr. Table 5 shows the measurement results of the wear volume and the friction coefficient obtained by this friction test.
[0020]
[Table 1]
[Table 2]
[Table 3]
[Table 4]
[Table 5]
【The invention's effect】
The wear-resistant hard sintered alloy of the present invention includes a WC-based cemented carbide containing a Ni-Cr-Mo alloy as a binder phase and a Co-bonded phase containing a Co 3 W 3 C composite compound. Compared to hard alloys, it has significantly better corrosion resistance and wear resistance, and its coefficient of friction tends to be low, so it requires wear resistance and is prone to corrosion. For example, nozzles for spraying solutions used in chemical plants, sludge treatment equipment, wet pulverization equipment, solutions mixed with gas or powder, effects as mechanical seals, and wear and corrosion resistance due to resin and ink It is expected to be effective as an injection mold that requires high performance and a ballpoint ball.
Claims (6)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29977396A JP4140928B2 (en) | 1996-10-24 | 1996-10-24 | Wear resistant hard sintered alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29977396A JP4140928B2 (en) | 1996-10-24 | 1996-10-24 | Wear resistant hard sintered alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10130771A JPH10130771A (en) | 1998-05-19 |
| JP4140928B2 true JP4140928B2 (en) | 2008-08-27 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29977396A Expired - Fee Related JP4140928B2 (en) | 1996-10-24 | 1996-10-24 | Wear resistant hard sintered alloy |
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| JP (1) | JP4140928B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002029193A (en) * | 2000-07-18 | 2002-01-29 | Mitsubishi Pencil Co Ltd | Ball for ballpoint pen tip |
| NL1016811C2 (en) | 2000-12-06 | 2002-06-13 | Skf Ab | Roller bearing comprising a part obtained with powder metallurgy technique. |
| JP5453727B2 (en) * | 2008-03-31 | 2014-03-26 | Ｊｆｅスチール株式会社 | Hot rolling method for steel strip |
| JP6182848B2 (en) * | 2012-10-30 | 2017-08-23 | ぺんてる株式会社 | Ball for ballpoint pen |
| JP2018001755A (en) * | 2016-06-23 | 2018-01-11 | 株式会社パイロットコーポレーション | Ball point pen |
| WO2024069774A1 (en) * | 2022-09-28 | 2024-04-04 | Ｔｐｒ株式会社 | Piston ring |
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1996
- 1996-10-24 JP JP29977396A patent/JP4140928B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
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| JPH10130771A (en) | 1998-05-19 |
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