JP2013128976A - Hardfacing welding material and machine parts having hardfacing welding layer using the same - Google Patents
Hardfacing welding material and machine parts having hardfacing welding layer using the same Download PDFInfo
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本発明は、例えば高温下で作動するディスク式バルブの摺動ガイド部等、潤滑剤を使用できない高温下での摺動部に耐摩耗性を付与する硬化肉盛層を設けるのに使用される硬化肉盛用溶接材料と、該材料による肉盛溶接層を有する機械部品に関する。 The present invention is used, for example, to provide a hardened layer for imparting wear resistance to a sliding part at a high temperature where a lubricant cannot be used, such as a sliding guide part of a disk type valve that operates at a high temperature. The present invention relates to a welding material for hardfacing and a machine part having a built-up welded layer made of the material.
一般的に、石油精製プラント等において高温流体を通す大流量流路の開閉部には、例えば図１に示すようなディスク式バルブが使用されている。このディスク式バルブは、配管接続用フランジ部Ｆ１，Ｆ２を備えたバルブケースＶ内の流路開閉部Ｒに対し、弁体としての厚板状のディスクＤを左右両側のガイドレールＧ，Ｇを介して進退移動させることにより、流路の遮蔽・開放を行うものである。しかして、左右各側のガイドレールＧは、図示のような上下一対の角棒体Ｓ，Ｓ（特許文献１）や、断面Ｌ字形のもの（特許文献２）からなるが、高温下での耐摩耗性を付与するために、例えば図２に示すガイドレールＧのように、母材１におけるディスクＤとの摺接ガイド面にトリバロイ（デロロ・ステライト社製の商品名）Ｔ−４００及びＴ−８００（以下、単にＴ−４００、Ｔ−８００と略称する）のようなＣｏ基合金やＮｉ基合金からなる高硬度の肉盛溶接層２を設けている。とりわけ、Ｔ−８００の肉盛溶接層は、高硬度であって、耐摩耗性、耐掻傷性、耐食性、低摩擦性等に優れる点から、広く採用されている。 In general, for example, a disk-type valve as shown in FIG. 1 is used in an open / close portion of a large flow path for passing a high-temperature fluid in an oil refinery plant or the like. This disc-type valve has a thick plate-like disc D as a valve element and guide rails G, G on both the left and right sides with respect to a flow path opening / closing portion R in a valve case V provided with flange portions F1, F2 for pipe connection. The channel is shielded / opened by moving forward / backward through the channel. Thus, the left and right guide rails G are composed of a pair of upper and lower rectangular bars S, S (Patent Document 1) as shown in the figure and an L-shaped cross section (Patent Document 2). In order to provide wear resistance, for example, as in the guide rail G shown in FIG. 2, tribaloid (trade names made by Deloro Stellite) T-400 and T A high-hardness overlay weld layer 2 made of a Co-base alloy or Ni-base alloy such as -800 (hereinafter simply referred to as T-400 or T-800) is provided. In particular, the build-up weld layer of T-800 is widely adopted because it has high hardness and is excellent in wear resistance, scratch resistance, corrosion resistance, low friction property, and the like.
上記のトリバロイ合金の概略組成は、質量％として、Ｔ−８００ではＭｏ：２８．５％、Ｃｒ８．５％、Ｓｉ：２．６％、Ｃ：０．０４％、残部Ｃｏ、Ｔ−４００ではＭｏ：２８．０％、Ｃｒ１８．０％、Ｓｉ：３．４％、Ｃ：０．０４％、残部Ｃｏとなっている。その肉盛溶接層の組織は、軟質なＣｏ基の固溶体マトリックス相と、硬い稠密六方晶系の金属間化合物であるＭｏ3Ｃｏ2Ｓｉのラーベス相との２相成分にて構成されている。 The approximate composition of the above-mentioned trivalloy alloy is, as mass%, for T-800, Mo: 28.5%, Cr 8.5%, Si: 2.6%, C: 0.04%, the balance Co, T-400 Mo: 28.0%, Cr 18.0%, Si: 3.4%, C: 0.04%, and the balance Co. The structure of the build-up weld layer is composed of a two-phase component of a soft Co-based solid solution matrix phase and a Laves phase of Mo 3 Co 2 Si, which is a hard dense hexagonal intermetallic compound.
一方、ディーゼルエンジンやガスエンジン等の給排気バルブのバルブフェース用の硬化肉盛用溶接材料では、従来汎用のＴ−４００に代わるＣｏ基合金として、質量（重量）％で、Ｃｒ：７．０〜１５．０％、Ｍｏ：２６〜３３％、Ｃ：０．１〜０．５％、Ｓｉ：２．０〜５．０％、Ｍｎ：０．０１〜１．０％、残部Ｃｏの組成を有するものも提案されている（特許文献３）。 On the other hand, in the case of a welding material for hardfacing for the valve face of a supply / exhaust valve such as a diesel engine or a gas engine, as a Co-based alloy replacing the conventional general-purpose T-400, the mass (weight)% is Cr: 7.0. -15.0%, Mo: 26-33%, C: 0.1-0.5%, Si: 2.0-5.0%, Mn: 0.01-1.0%, balance Co composition Have also been proposed (Patent Document 3).
しかるに、Ｔ−８００やＴ−４００の硬化肉盛用溶接材料は、溶接施工時の割れ感受性が高く、複雑形状への溶接施工や多層盛溶接が難しく、また表面硬度のばらつきを生じやすいという難点がある上、近年において前記ディスク式バルブのガイドレール等のように高温下で金属部材同士が摺接する部位に要望される更に高レベルの耐摩耗性、耐亀裂・欠損性には対応できなかった。一方、前記提案に係るＣｏ基合金の硬化肉盛用溶接材料においても、同様に高温下で金属部材同士が摺接する部位に要望される高レベルの耐摩耗性、耐亀裂・欠損性には対応できない。 However, T-800 and T-400 hardfacing welding materials are highly susceptible to cracking during welding, difficult to weld into complex shapes and multi-layer welding, and difficult to cause variations in surface hardness. In addition, in recent years, it has not been possible to cope with the higher level of wear resistance, crack resistance and chipping required for parts where the metal members slide in contact with each other at high temperatures, such as the guide rail of the disk type valve in recent years. . On the other hand, in the welding materials for hardfacing of Co-based alloys according to the above proposal, the high level of wear resistance, crack resistance and fracture resistance required for the parts where metal members slide in contact at high temperatures are also supported. Can not.
本発明は、上述の事情に鑑みて、高硬度でばらつきが小さく、前記ガイドレール等として卓越した耐摩耗性を発揮する肉盛溶接層を形成でき、且つ溶接性や肉盛溶接層の機械加工性にも優れるＣｏ基合金系の硬化肉盛用溶接材料と、それによる肉盛溶接層を備えた機械部品を提供することを目的としている。 In view of the above circumstances, the present invention is capable of forming a built-up weld layer that exhibits high wear resistance and small variation as a guide rail, and has excellent weld resistance. An object of the present invention is to provide a Co-base alloy-based hardfacing welding material having excellent properties and a machine part including the overlay welding layer.
上記目的を達成するために、請求項１の発明に係る硬化肉盛用溶接材料は、Ｃｏ基合金であって、Ｃが０．６〜１．０質量％、Ｓｉが２．０〜５．０質量％、Ｗ，Ｎｂ，Ｔｉから選ばれる少なくとも一種が合量で０．５〜１．０質量％、Ｃｒが１６．０〜２０．０質量％、Ｍｏが２０．０〜３５．０質量質量％、Ｎｉが２．０質量％以下、Ｆｅが２．０質量％以下、残部が実質的にＣｏである組成を有するものとしている。 In order to achieve the above object, the welding material for hardfacing according to the invention of claim 1 is a Co-based alloy, wherein C is 0.6 to 1.0% by mass and Si is 2.0 to 5. 0% by mass, at least one selected from W, Nb, and Ti is 0.5 to 1.0% by mass in total, Cr is 16.0 to 20.0% by mass, and Mo is 20.0 to 35.0% by mass. It is assumed that the composition has a mass%, Ni is 2.0 mass% or less, Fe is 2.0 mass% or less and the balance is substantially Co.
また、請求項２の発明に係る機械部品は、高温下での金属同士の摺接部を構成する金属母材の摺接面に、請求項１に記載の硬化肉盛用溶接材料による厚さ２．５〜５ｍｍでビッカース硬度（Ｈｖ）７００以上の肉盛溶接層が形成されてなるものとしている。 Further, the mechanical part according to the invention of claim 2 has a thickness by the welding material for hardfacing according to claim 1 on the sliding contact surface of the metal base material constituting the sliding contact portion between the metals at high temperature. A build-up weld layer having a Vickers hardness (Hv) of 700 or more at 2.5 to 5 mm is formed.
請求項１の発明によれば、Ｃｏ基合金系の硬化肉盛用溶接材料として、特定種の元素を特定範囲で含むことで、溶融金属の凝固時における固液相間の温度領域が拡大すると共に冷却速度も遅くなり、不活性ガスシールド下でも金属間化合物（Ｍｏ3Ｃｏ2Ｓｉ)結晶が多く析出して且つ複合炭化物の微細結晶も析出し、組織全体に小さい結晶粒子が分散して硬度的に安定するため、特に高温下でも高硬度であって、且つ硬度のばらつきが小さく、ディスク式バルブのガイドレール等として卓越した耐摩耗性を発揮でき、耐掻傷性、耐食性、低摩擦性、溶接性、機械加工性等にも優れた肉盛溶接層を形成できるものが提供される。 According to the first aspect of the present invention, the temperature range between the solid and liquid phases at the time of solidification of the molten metal is expanded by including a specific type of element in a specific range as a welding material for hardening buildup of a Co-based alloy system. At the same time, the cooling rate is reduced, and even under an inert gas shield, a large amount of intermetallic compound (Mo 3 Co 2 Si) crystals are precipitated, and fine crystals of composite carbides are also precipitated. In particular, it has high hardness even at high temperatures and has a small variation in hardness, and can exhibit excellent wear resistance as a guide rail for disc-type valves. Scratch resistance, corrosion resistance, and low friction A material capable of forming a built-up weld layer excellent in weldability and machinability is also provided.
請求項２の発明によれば、ディスク式バルブのガイドレールのように高温下での摺接部を構成する金属部品として、その金属母材の摺接面に上記硬化肉盛用溶接材料による特定厚みで高硬度の肉盛溶接層が形成されていることから、摺接部が低摩擦で耐摩耗性、耐掻傷性、耐食性に優れるものが提供される。 According to the second aspect of the present invention, as the metal part constituting the sliding contact portion at a high temperature like the guide rail of the disc type valve, the sliding contact surface of the metal base material is specified by the welding material for hardfacing. Since the build-up weld layer having a high hardness in thickness is formed, a sliding contact portion having low friction and excellent wear resistance, scratch resistance, and corrosion resistance is provided.
本発明の硬化肉盛用溶接材料は、既述のように、Ｃｏ（コバルト）基合金であって、Ｃ（炭素）が０．６〜１．０質量％、Ｓｉ（珪素）が２．０〜５．０質量％、Ｗ（タングステン），Ｎｂ（ニオブ），Ｔｉ（チタニウム）より選ばれる少なくとも一種が合量で０．５〜１．０質量％、Ｃｒ（クロム）が１６．０〜２０．０質量％、Ｍｏ（モリブデン）が２０．０〜３５．０質量質量％、Ｎｉ（ニッケル）が２．０質量％以下、Ｆｅ（鉄）が２．０質量％以下、残部が実質的にＣｏからなる組成を有するものである。 As described above, the welding material for hardfacing according to the present invention is a Co (cobalt) based alloy, and C (carbon) is 0.6 to 1.0% by mass, and Si (silicon) is 2.0. -5.0 mass%, at least one selected from W (tungsten), Nb (niobium), Ti (titanium) is 0.5-1.0 mass% in total, and Cr (chromium) is 16.0-20 0.0 mass%, Mo (molybdenum) is 20.0-35.0 mass%, Ni (nickel) is 2.0 mass% or less, Fe (iron) is 2.0 mass% or less, and the balance is substantially the same. It has a composition made of Co.
そして、この硬化肉盛用溶接材料によって基材表面に肉盛溶接した溶着金属は、Ｃｏ，Ｍｏ，Ｃｒ，Ｓｉの４元系合金相に、金属間化合物であるＭｏ3Ｃｏ2Ｓｉの結晶と、Ｍｏ及びＣｒとＷ，Ｎｂ，Ｔｉ等の複合炭化物の微細結晶とが分散した複合組織になっており、高度の耐熱性、耐摩耗性、耐食性を示すと共に、優れた高温硬度を備えている。これは、マトリックス中のＭｏ，Ｃｒ等の固溶によって高耐食性がもたらされ、またマトリックスに分散する硬質な金属間化合物（Ｍｏ3Ｃｏ2Ｓｉ）の自己潤滑性によって耐摩耗性が高められ、更にＭｏ−Ｃｒ−Ｗ複合炭化物の微細結晶の分散効果として高硬度、特に高温下での高硬度が付与されて且つ硬度のばらつきが少なくなるものと想定される。 The weld metal that has been welded to the surface of the base material by this welding material for hardfacing is composed of Mo 3 Co 2 Si crystals, which are intermetallic compounds, in a quaternary alloy phase of Co, Mo, Cr, and Si. , Mo and Cr have a composite structure in which fine crystals of composite carbides such as W, Nb, and Ti are dispersed, exhibiting high heat resistance, wear resistance, corrosion resistance, and excellent high temperature hardness . This is because the high corrosion resistance is brought about by the solid solution of Mo, Cr, etc. in the matrix, and the wear resistance is enhanced by the self-lubricating property of the hard intermetallic compound (Mo 3 Co 2 Si) dispersed in the matrix, Furthermore, it is assumed that high hardness, particularly high hardness at high temperatures, is imparted as an effect of dispersing fine crystals of the Mo—Cr—W composite carbide, and variation in hardness is reduced.
上記組成中のＣは、Ｍｏ及びＣｒとＷ，Ｎｂ，Ｔｉ等との間で複合炭化物を形成する成分であり、その添加量が０．６質量％以上と従来汎用のＴ−８００に比較して略一桁多く、それによって多く析出した微細結晶の分散効果により、合金の硬度及び耐摩耗性を高め、また高温強度の向上に大きく寄与する。しかるに、その添加量は、多過ぎては複合炭化物の生成が過剰になって合金の脆化を招き、割れや欠けを発生し易くなるため、１．０質量％を上限とする。 C in the above composition is a component that forms a composite carbide between Mo and Cr and W, Nb, Ti, etc., and its added amount is 0.6% by mass or more compared to the conventional general-purpose T-800. The effect of dispersing fine crystals precipitated by an order of magnitude, thereby increasing the hardness and wear resistance of the alloy and greatly contributing to the improvement of the high temperature strength. However, if the addition amount is too large, the composite carbide is excessively produced and the alloy becomes brittle, and cracks and chips are likely to occur.
Ｓｉは、合金の融点を下げて溶融金属の流動性を高める成分であり、その作用を十分に発揮する上で２．０質量％以上の添加を必要とするが、多過ぎては金属間化合物のＣｏ−Ｍｏ−Ｓｉ相が生成過剰になって合金の脆化を招くことから、添加量の上限を５．０質量％とする。 Si is a component that lowers the melting point of the alloy and increases the fluidity of the molten metal, and in order to fully exert its action, it needs to be added in an amount of 2.0% by mass or more. Since the Co—Mo—Si phase of the alloy is excessively formed and the alloy is embrittled, the upper limit of the addition amount is 5.0 mass%.
Ｗ，Ｎｂ，Ｔｉは、Ｍｏ及びＣｒと共に複合炭化物を形成する成分であって、該複合炭化物としてマトリックス中に分散し易い微細結晶を生成させて割れや欠け防止に寄与すると共に、特に硬度を大きく高める作用を発揮する。これらの添加量は合量で、０．５質量％未満では十分な添加効果が得られず，逆に１．０質量％を超えると溶融金属の流動性を低下させる。なお、Ｗ，Ｎｂ，Ｔｉの内、特にＷが添加効果の上で最適なものとして推奨される。 W, Nb, and Ti are components that form a composite carbide together with Mo and Cr. As the composite carbide, fine crystals that easily disperse in the matrix are generated, contributing to prevention of cracking and chipping, and particularly high hardness. Demonstrate the effect of increasing. These addition amounts are a total amount, and if the amount is less than 0.5% by mass, a sufficient addition effect cannot be obtained. Conversely, if the amount exceeds 1.0% by mass, the fluidity of the molten metal is lowered. Of W, Nb, and Ti, W is particularly recommended as the optimum in terms of the effect of addition.
Ｍｏは、Ｃｏ，Ｃｒ，Ｓｉと共に前記の４元系合金相を形成し、且つＣｏ及びＳｉと共に前記金属間化合物の結晶を析出し、該金属間化合物の高い硬度と自己潤滑性によって合金の耐摩耗性を高め、また耐食性を向上させる成分である。その添加量は、２０．０質量％未満では金属間化合物の析出量が不足し、多くなるほど該析出量が増加するが、多過ぎてはＣｏ基合金としてのバランスを悪化させるので３５．０質量％を上限とする。 Mo forms the quaternary alloy phase with Co, Cr, Si, and precipitates crystals of the intermetallic compound together with Co and Si, and the resistance of the alloy is improved by the high hardness and self-lubricity of the intermetallic compound. It is a component that improves wear resistance and improves corrosion resistance. If the addition amount is less than 20.0% by mass, the amount of precipitation of intermetallic compounds is insufficient, and the amount of precipitation increases as the amount increases. % Is the upper limit.
Ｃｒは、Ｃｏ，Ｍｏ，Ｓｉと共に前記の４元系合金相を形成する成分であり、その添加によって特に合金の硬度及び耐食性を高める作用を発揮する。その添加量は、１６．０質量％未満では合金の耐食性及び耐熱性が不足すると共に硬度及び靱性も低下する一方、２０．０質量％を超えても合金の靱性が低下して割れや欠けを発生し易くなる。 Cr is a component that forms the quaternary alloy phase together with Co, Mo, and Si, and exhibits the effect of increasing the hardness and corrosion resistance of the alloy in particular when added. If the amount added is less than 16.0% by mass, the corrosion resistance and heat resistance of the alloy are insufficient and the hardness and toughness are also reduced. On the other hand, if it exceeds 20.0% by mass, the toughness of the alloy is reduced and cracks and chips are not caused. It tends to occur.
Ｃｏは、Ｃｏ基合金としての基本元素であり、上記諸元素と共に、高耐食性、高耐熱性、高耐摩耗性、高靱性の合金を形成する。 Co is a basic element as a Co-based alloy and forms an alloy having high corrosion resistance, high heat resistance, high wear resistance, and high toughness together with the above elements.
Ｆｅ及びＮｉは、本発明の意図する合金特性面からは不要な不純分に相当する元素であるため、その混在量が少ないほどよいが、それぞれ２．０質量％までの範囲であれば特性的に許容される。 Fe and Ni are elements corresponding to impurities that are unnecessary in terms of the alloy characteristics intended by the present invention, so the smaller the mixing amount, the better. Is acceptable.
なお、本発明の硬化肉盛用溶接材料は、上記諸元素以外の元素についても、不可避不純物あるいは付随不純物として０．１質量％以下の微量の範囲で含んでいてもよい。 In addition, the welding material for hardfacing of this invention may also contain elements other than the said elements in the trace amount range of 0.1 mass% or less as an inevitable impurity or an accompanying impurity.
このような硬化肉盛用溶接材料による肉盛溶接手段としては、特に制約はなく、不活性ガスシールド下で行うアーク溶接であるプラズマ粉末溶接法やＴＩＧ（タングステン・イナートガス）溶接法、酸素アセチレンガス溶接法等の種々の方法を採用できるが、特にプラズマ粉末溶接法が高い生産性を得る上で好適である。 The build-up welding means using such a welding material for hardening build-up is not particularly limited, and is a plasma powder welding method such as arc welding performed under an inert gas shield, a TIG (tungsten inert gas) welding method, an oxygen acetylene gas. Various methods such as a welding method can be employed, but the plasma powder welding method is particularly suitable for obtaining high productivity.
本発明の硬化肉盛用溶接材料による肉盛溶接の適用対象には特に制約はなく、例えば自動車、船舶、航空機、コンプレッサー、石油精プラント等で用いられる軸受部材、ピストン部材、シール部材、バルブ部材等の高い耐摩耗性が要求される各種部材、とりわけ金属同士の摺接部、潤滑剤が行き渡りにくい摺接部、高温下で潤滑剤を使用できない摺接部等を構成する部材が好適である。そして、これらの中でも特に適用効果が大きいのは、高温下で作動するディスク式バルブの摺動ガイド部等、潤滑剤を使用できない高温下での金属同士の摺接部を構成する部材である。 There are no particular restrictions on the application target of overlay welding with the welding material for hardening overlay of the present invention, for example, bearing members, piston members, seal members, valve members used in automobiles, ships, aircraft, compressors, petroleum refineries, etc. Various members that require high wear resistance, such as a sliding contact portion between metals, a sliding contact portion where lubricant is difficult to spread, and a sliding contact portion where a lubricant cannot be used at high temperatures are particularly suitable. . Among these, the members that constitute the sliding contact portion between the metals at a high temperature at which the lubricant cannot be used, such as a sliding guide portion of a disk type valve that operates at a high temperature, are particularly effective.
しかして、本発明の機械部品は、高温下での金属同士の摺接部を構成する金属母材の摺接面に、上記の硬化肉盛用溶接材料による厚さ２．５〜５ｍｍでビッカース硬度（Ｈｖ）７００以上の肉盛溶接層が形成されてなるものとしている。この肉盛溶接層の厚さは、２．５ｍｍ未満では十分な耐久性が得られず、５ｍｍを超える厚みでは施工性に劣ると共に材料コスト的に不経済である。 Thus, the mechanical component of the present invention has a Vickers thickness of 2.5 to 5 mm by the above-mentioned welding material for hardfacing on the sliding contact surface of the metal base material constituting the sliding contact portion between the metals at high temperature. A build-up weld layer having a hardness (Hv) of 700 or more is formed. If the thickness of the overlay weld layer is less than 2.5 mm, sufficient durability cannot be obtained, and if the thickness exceeds 5 mm, the workability is inferior and the material cost is uneconomical.
後記表１に示す合金組成の粉末溶接材料Ａ１〜Ａ３（実施例）及びＢ１〜Ｂ１０（比較例）を用い、プラズマ粉末溶接法により、ＳＵＳ３０８鋼材（幅５０ｍｍ・厚さ３０ｍｍ・長さ３００ｍｍ）の表面に、溶接ビードの厚さ５ｍｍ、幅３０ｍｍ、長さ２５０ｍｍの肉盛溶接を行った後、該肉盛溶接層の表面を層厚が４ｍｍになるまでダイアモンド砥粒による荒研磨及びバフ研磨を行って鏡面仕上げした。なお、粉末溶接材料Ｂ１０はＴ−８００の合金組成である。 Using powder welding materials A1 to A3 (Examples) and B1 to B10 (Comparative Examples) of alloy compositions shown in Table 1 below, SUS308 steel (width 50 mm, thickness 30 mm, length 300 mm) was formed by plasma powder welding. After performing overlay welding with a weld bead thickness of 5 mm, width of 30 mm, and length of 250 mm on the surface, rough polishing and buffing with diamond abrasive grains are performed on the surface of the build-up weld layer until the layer thickness reaches 4 mm. I went to the mirror finish. The powder welding material B10 has a T-800 alloy composition.
〔表面硬度試験１〕
粉末溶接材料Ａ１〜Ａ３及びＢ１〜Ｂ１０にて形成した各肉盛溶接層の表面のショアー硬度（Ｈｓ）を、ハンディ硬さ計（ＪＦＥアドバンテック社製の商品名SONOHARD HS-21型）を用いて測定した。その結果を後記表１に示す。なお、硬度のばらつきと平均は、各肉盛溶接層の試料１０点の測定値に基づく。
[Surface hardness test 1]
The Shore hardness (Hs) of the surface of each build-up weld layer formed with the powder welding materials A1 to A3 and B1 to B10 is measured using a handy hardness meter (trade name SONOHARD HS-21 manufactured by JFE Advantech). It was measured. The results are shown in Table 1 below. In addition, the dispersion | variation and average of hardness are based on the measured value of 10 samples of each build-up welding layer.
上記表１で示すように、本発明の硬化肉盛用溶接材料（粉末溶接材料Ａ１〜Ａ３）による肉盛溶接層の表面硬度は、ショアー硬度（Ｈｓ）として、Ｔ−８００（粉末溶接材料Ｂ１０）による肉盛溶接層に比較して格段に高い上にばらつきも少ないことが明らかである。また、本発明とは合金組成の元素比率が多少異なる硬化肉盛用溶接材料（粉末溶接材料Ｂ１〜Ｂ９）による肉盛溶接層の表面硬度は、ばらつきが比較的に少なくても本発明によるものよりも低くなることが判る。 As shown in Table 1 above, the surface hardness of the build-up welded layer by the welding material for hardfacing (powder welding materials A1 to A3) of the present invention is T-800 (powder welding material B10) as Shore hardness (Hs). It is clear that it is much higher and has less variation than the overlay welded layer. In addition, the surface hardness of the overlay welding layer made of the welding material for hardfacing (powder welding materials B1 to B9) having a slightly different element ratio of the alloy composition from the present invention is according to the present invention even if the variation is relatively small. It turns out that it becomes lower than.
〔表面硬度試験２〕
表１の粉末溶接材料Ａ１，Ｂ１０による各肉盛溶接層の表面のビッカース硬度（Ｈｖ）を、ビッカース硬度計によって２ｍｍ間隔で測定したところ、図５に示す結果が得られた。この図３より、本発明の硬化肉盛用溶接材料による肉盛溶接層の表面硬度は、ビッカース硬度（Ｈｖ）においても、従来汎用の硬化肉盛用溶接材料（Ｔ−８００）に比較して格段に高く且つばらつきが非常に少ないことが判る。
[Surface hardness test 2]
When the Vickers hardness (Hv) of the surface of each build-up weld layer by the powder welding materials A1 and B10 in Table 1 was measured at 2 mm intervals with a Vickers hardness meter, the results shown in FIG. 5 were obtained. From FIG. 3, the surface hardness of the overlay welded layer by the welding material for hardfacing according to the present invention is also in the Vickers hardness (Hv), compared to the conventional general-purpose welding material for hardfacing (T-800). It can be seen that it is much higher and has very little variation.
〔溶着金属の組織観察〕
表１の粉末溶接材料Ａ１，Ｂ１０による溶着金属の組織を走査型電子顕微鏡によって観察した。図３（ａ）（ｂ）は粉末溶接材料Ｂ１０による電子顕微鏡写真、図４（ａ）（ｂ）は粉末溶接材料Ａ１による電子顕微鏡写真である。図３（ａ）（ｂ）から明らかなように、粉末溶接材料Ｂ１０による溶着金属組織では、硬い稠密六方晶系のラーベス相（金属間化合物Ｍｏ3Ｃｏ2Ｓｉ）と、比較的軟らかいマトリックス相（共晶組織）との２相成分から構成されているが、凝固時の固液相間の温度領域が狭いため、金属間化合物は析出量が少ない上に大きな結晶粒子になり、これによって硬度のばらつきが大きくなると推測される。これに対し、本発明の硬化肉盛用溶接材料による溶着金属組織では、図４（ａ）（ｂ）から明らかなように、凝固時の固液相間の温度領域が拡大すると共に冷却速度も遅くなるため、金属間化合物が小さい結晶粒子として多く析出することに加えて複炭化物の微細結晶も多く析出し、これら金属間化合物と複炭化物の結晶粒子が組織全体に均一分散して硬度的に安定すると想定される。
[Observation of weld metal structure]
The structure of the deposited metal by the powder welding materials A1 and B10 in Table 1 was observed with a scanning electron microscope. 3A and 3B are electron micrographs of the powder welding material B10, and FIGS. 4A and 4B are electron micrographs of the powder welding material A1. As is apparent from FIGS. 3A and 3B, in the weld metal structure of the powder welding material B10, a hard dense hexagonal Laves phase (intermetallic compound Mo 3 Co 2 Si) and a relatively soft matrix phase ( Although the temperature region between the solid and liquid phases at the time of solidification is narrow, the intermetallic compound has a small amount of precipitation and becomes large crystal grains, which makes it It is estimated that the variation becomes large. On the other hand, in the welded metal structure by the welding material for hardfacing according to the present invention, as apparent from FIGS. 4 (a) and 4 (b), the temperature region between the solid and liquid phases during solidification is expanded and the cooling rate is also increased. In addition to the precipitation of many intermetallic compounds as small crystal particles, many fine crystals of double carbides are also precipitated, and these intermetallic compounds and double carbide crystal particles are uniformly dispersed throughout the entire structure to increase hardness. It is assumed to be stable.
〔高温硬さ試験〕
表１の粉末溶接材料Ａ１，Ｂ１０による肉盛溶接層の各試料５点について、高温顕微鏡硬度計を用い、荷重１ｋｇｆにおいて常温から８００℃までの表面硬度（ビッカース硬度Ｈｖ）を測定したところ、図７に示す結果が得られた。なお、図７のビッカース硬度（Ｈｖ）の数値は試料５点の平均値である。この試験結果から、本発明の硬化肉盛用溶接材料による肉盛溶接層は、常温から８００℃までの温度範囲の全域にわたり、従来汎用の硬化肉盛用溶接材料（Ｔ−８００）による肉盛溶接層よりも高い表面硬度を示すことが明らかである。
[High temperature hardness test]
The surface hardness (Vickers hardness Hv) from room temperature to 800 ° C. was measured at a load of 1 kgf using a high-temperature microscope hardness meter for each of the five samples of the build-up weld layer made of the powder welding materials A1 and B10 in Table 1. The result shown in 7 was obtained. In addition, the numerical value of Vickers hardness (Hv) of FIG. 7 is an average value of five samples. From this test result, the build-up weld layer by the welding material for hardfacing of the present invention covers the entire temperature range from room temperature to 800 ° C., and is built-up by the conventional general-purpose welding material for hardfacing (T-800). It is clear that the surface hardness is higher than the weld layer.
〔耐摩耗性試験〕
表１の粉末溶接材料Ａ１，Ｂ１０による肉盛溶接層について、スガ式摩耗試験機（型式：ＮＵＳ−ＩＳＯ−３）を用いて下記条件で摩耗試験を行い、各摩耗回数による摩耗溝の断面の面積（μｍ2)を測定した。その結果を図６に示す。
摩耗紙の砥粒材質： ＳｉＣ
摩耗紙粗さ： ＃３２０
摩耗輪幅： １２ｍｍ
１往復毎の摩耗輪回転角度：０．９ｄｅｇ／１回往復
試験辺走査ストローク拒理：１０ｍｍ
垂直負荷： ３０００ｇ・ｆ
走査平均速度： ４００ｍｍ／分
摩耗往復数： １６００往復（４×４００回往復）
[Abrasion resistance test]
About the build-up weld layer by powder welding material A1, B10 of Table 1, a wear test is performed on the following conditions using a Suga type wear tester (model: NUS-ISO-3), and the cross section of the wear groove by each wear frequency The area (μm 2 ) was measured. The result is shown in FIG.
Abrasive paper abrasive material: SiC
Abrasion paper roughness: # 320
Wear wheel width: 12mm
Wear wheel rotation angle for each reciprocation: 0.9 deg / reciprocation test edge scanning stroke rejection: 10 mm
Vertical load: 3000g · f
Scanning average speed: 400 mm / min Wear reciprocation number: 1600 reciprocations (4 × 400 reciprocations)
図６で示す摩耗試験結果から、本発明の硬化肉盛用溶接材料による肉盛溶接層は、従来汎用の硬化肉盛用溶接材料（Ｔ−８００）による肉盛溶接よりも高い耐摩耗性を具備することが判る。 From the results of the wear test shown in FIG. 6, the build-up welded layer by the welding material for hardfacing according to the present invention has higher wear resistance than the conventional overlay welding by the welding material for hardfacing (T-800). It turns out that it has.
〔溶接性〕
表１の粉末溶接材料Ａ１〜Ａ３，Ｂ１０について肉盛溶接時の挙動を観察したところ、粉末溶接材料Ａ１〜Ａ３は、従来汎用の粉末溶接材料Ｂ１０（Ｔ−８００）に比較し、溶融時の溶融プールの濡れ性が非常によく、溶接ビード端面も良好であるため、割れ等の溶接欠陥を生じにくいことが確認された。また、多層肉盛溶接（２層盛り）の場合、粉末溶接材料Ｂ１０では２層目の溶融プールの濡れ性が１層目よりも悪くなるのに対し、粉末溶接材料Ａ１〜Ａ３では１層目と２層目の溶融プールの濡れ性は変わらず良好であり、多層肉盛溶接への適用性にも優れることが判明した。
(Weldability)
When the behavior at the time of overlay welding was observed for the powder welding materials A1 to A3 and B10 in Table 1, the powder welding materials A1 to A3 were compared with the conventional general-purpose powder welding material B10 (T-800), and at the time of melting. It was confirmed that the weldability of the molten pool is very good and the weld bead end face is also good, so that it is difficult to cause weld defects such as cracks. In addition, in the case of multilayer overlay welding (two-layer overlay), the wettability of the molten pool of the second layer is worse than that of the first layer in the powder welding material B10, whereas the first layer is in the powder welding materials A1 to A3. It was found that the wettability of the molten pool of the second layer was still good and the applicability to multilayer overlay welding was also excellent.
〔加工性〕
表１の粉末溶接材料Ａ１〜Ａ３，Ｂ１０による各肉盛溶接を施したＳＵＳ３０８鋼材について、フライス加工を行ったところ、相互の加工性に遜色はなく、またいずれも欠陥は発生しなかったが、粉末溶接材料Ａ１〜Ａ３の方が粉末溶接材料Ｂ１０よりも切断面の光沢に勝るように感じられた。
[Processability]
About SUS308 steel materials subjected to overlay welding with powder welding materials A1 to A3 and B10 of Table 1, when milling was performed, the mutual workability was not inferior, and no defects occurred, It was felt that the powder welding materials A1 to A3 were superior to the gloss of the cut surface than the powder welding material B10.
１ 母材
２ 肉盛溶接層
Ｇ ガイドレール（摺接部）
Ｓ 角棒体（機械部品）
1 Base material 2 Overlay welding layer G Guide rail (sliding contact part)
S square bar (machine parts)
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| CN106334900A (en) * | 2016-10-27 | 2017-01-18 | 辽宁工程技术大学 | Overlaying welding repair method used for worn middle plate of middle slot of scraper conveyer |
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| JPH0584592A (en) * | 1991-09-27 | 1993-04-06 | Toyota Motor Corp | Cobalt-based filling alloy excellent in wear resistance and opponent attackability |
| JPH05131289A (en) * | 1991-11-12 | 1993-05-28 | Daido Steel Co Ltd | Welding material for hard build-up |
| JPH07300642A (en) * | 1994-04-27 | 1995-11-14 | Nittetsu Hard Kk | Coating material and metal bath immersion member coated with this material |
| JPH09271983A (en) * | 1996-04-03 | 1997-10-21 | Kubota Corp | Material for sliding part build up welding |
| JP2007533842A (en) * | 2003-07-30 | 2007-11-22 | ダイムラークライスラー・アクチェンゲゼルシャフト | Valve seat ring made of Co base or Co / Mo base alloy and method for manufacturing the same |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0584592A (en) * | 1991-09-27 | 1993-04-06 | Toyota Motor Corp | Cobalt-based filling alloy excellent in wear resistance and opponent attackability |
| JPH05131289A (en) * | 1991-11-12 | 1993-05-28 | Daido Steel Co Ltd | Welding material for hard build-up |
| JPH07300642A (en) * | 1994-04-27 | 1995-11-14 | Nittetsu Hard Kk | Coating material and metal bath immersion member coated with this material |
| JPH09271983A (en) * | 1996-04-03 | 1997-10-21 | Kubota Corp | Material for sliding part build up welding |
| JP2007533842A (en) * | 2003-07-30 | 2007-11-22 | ダイムラークライスラー・アクチェンゲゼルシャフト | Valve seat ring made of Co base or Co / Mo base alloy and method for manufacturing the same |
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| CN106334900A (en) * | 2016-10-27 | 2017-01-18 | 辽宁工程技术大学 | Overlaying welding repair method used for worn middle plate of middle slot of scraper conveyer |
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