JP5834372B2 - Method for producing Fe-Cu-C sintered material - Google Patents
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この発明は、高価な合金元素の使用を極力抑えて焼結後の硬度・強度を高めた生産性にも優れるＦｅ−Ｃｕ−Ｃ系焼結材料の製造方法に関する。 The present invention relates to a method for producing a Fe—Cu—C-based sintered material that is excellent in productivity by suppressing the use of an expensive alloy element as much as possible and increasing the hardness and strength after sintering.
Ｆｅ−Ｃｕ−Ｃ系の焼結材料は、粉末の成形、焼結、サイジングの工程を経た後に熱処理を行なって硬度及び強度を高める方法が通常採られている。 For Fe—Cu—C-based sintered materials, a method is generally employed in which heat treatment is performed after powder forming, sintering, and sizing steps to increase the hardness and strength.
Ｎｉ、Ｍｏ、Ｃｏ、Ｍｎ、Ｃｒなどの合金元素を添加して焼入れ性を向上させて硬度や強度を高めることもなされている。例えば、Ｆｅ−６Ｎｉ−１Ｃｕ−０．５Ｍｏ−０．５５Ｃの組成の焼結材料は、一般的な焼結炉の冷却速度でマルテンサイト組織を得られると言われている。 Alloy elements such as Ni, Mo, Co, Mn, and Cr are added to improve hardenability and increase hardness and strength. For example, it is said that a sintered material having a composition of Fe-6Ni-1Cu-0.5Mo-0.55C can obtain a martensite structure at a cooling rate of a general sintering furnace.
また、下記特許文献１に開示されるようなセラミックス含有のＦｅ−Ｃｕ−Ｃ系焼結材料も提案されている。 Further, a ceramic-containing Fe—Cu—C based sintered material as disclosed in Patent Document 1 below has also been proposed.
Ｆｅ−Ｃｕ−Ｃ系焼結材料の高硬度化のために従来添加されている合金元素は高価である。従って、その高価な合金元素を極力使用せずに材料の硬度を高めることが望まれる。 Conventionally added alloy elements for increasing the hardness of Fe-Cu-C sintered materials are expensive. Therefore, it is desired to increase the hardness of the material without using the expensive alloy element as much as possible.
でき得るならば、サイジング後の熱処理工程も省略することも望まれる。そこで、流れ作業での焼結が行なえる従来のベルト焼結炉を使用し、その炉による焼結の終段においてシンターハードニングを実施することを検討した。 If possible, it is also desirable to omit the heat treatment step after sizing. Therefore, a conventional belt sintering furnace capable of performing sintering in a flow operation was used, and it was examined that sintering hardening was performed at the final stage of sintering in the furnace.
ところが、ベルト焼結炉は、強制冷却装置を採用しても冷却速度がせいぜい０．５〜１．０℃／ｓｅｃ程度であり、このような速度では満足できる硬度、強度改善の効果を期待できない。 However, the belt sintering furnace has a cooling rate of about 0.5 to 1.0 ° C./sec at most even if a forced cooling device is employed, and satisfactory effects of hardness and strength cannot be expected at such a rate. .
なお、バッチ式焼結炉を用いれば、焼結温度に加熱した材料を冷却液に浸漬してマルテンサイト相を生じさせることができるが、このバッチ式焼結炉では生産性が高まらない。 If a batch-type sintering furnace is used, a material heated to a sintering temperature can be immersed in a cooling liquid to generate a martensite phase. However, productivity does not increase in this batch-type sintering furnace.
また、鉄系焼結材料は、焼結後にスチーム処理を行って鉄の酸化被膜を生じさせる方法で表面の硬度を高めることができるが、この方法では、強度を高めることができない。 Further, the iron-based sintered material can be increased in surface hardness by a method of performing a steam treatment after sintering to produce an iron oxide film, but this method cannot increase the strength.
この発明は、かかる現状技術に鑑みてなされたものであって、高価な合金元素の使用を極力抑えながら生産性に優れた方法でＦｅ−Ｃｕ−Ｃ系焼結材料の硬度・強度を高めることを課題としている。 The present invention has been made in view of the present state of the art, and increases the hardness and strength of the Fe—Cu—C based sintered material by a method excellent in productivity while suppressing the use of expensive alloy elements as much as possible. Is an issue.
上記の課題を解決するため、原料粉末を加圧成形して得られた成形体の焼結をローラハース炉を使用して行い、炉内において焼結温度に加熱した後に８３０℃〜９００℃まで冷却し、その後、２．５℃／ｓｅｃ〜４．０℃／ｓｅｃの速度で急冷するＣｕの含有率が０より多くて３．０ｗｔ％以下、Ｃの含有率が０．２〜１．０ｗｔ％、残Ｆｅの組成のＦｅ−Ｃｕ−Ｃ系焼結材料の製造方法を提供する。 In order to solve the above-mentioned problems, the green body obtained by pressure-molding the raw material powder is sintered using a roller hearth furnace, heated to the sintering temperature in the furnace, and then cooled to 830 ° C. to 900 ° C. Thereafter, the Cu content rapidly quenched at a rate of 2.5 ° C./sec to 4.0 ° C./sec is more than 0 and 3.0 wt% or less, and the C content is 0.2 to 1.0 wt%. A method for producing an Fe—Cu—C based sintered material having a composition of residual Fe is provided.
その方法で得られる焼結材料は、フェライトと、パーライト中のセメンタイト相の析出間隔が５００ｎｍ以下の微細パーライトとが混在した組織を有する。 Sintered material obtained by the method, that Yusuke and ferrite, the deposition interval of cementite phase in the pearlite are mixed and the following fine pearlite 500nm tissue.
この発明のＦｅ−Ｃｕ−Ｃ系焼結材料の製造方法によれば、優れた生産性を確保しながら得られるＦｅ−Ｃｕ−Ｃ系焼結材料の硬度を高めることができる。 According to the method for producing an Fe—Cu—C based sintered material of the present invention, the hardness of the Fe—Cu—C based sintered material obtained while ensuring excellent productivity can be increased.
以下、この発明のＦｅ−Ｃｕ−Ｃ系焼結材料の製造方法の実施の形態を、添付図面の図１〜図８に基づいて説明する。 Embodiments of a method for producing an Fe—Cu—C based sintered material according to the present invention will be described below with reference to FIGS.
この発明のＦｅ−Ｃｕ−Ｃ系焼結材料の製造方法では、原料粉末を加圧成形して得られた成形体の焼結を、ローラハース炉（連続焼結炉）を使用して行う。 In the method for producing an Fe—Cu—C-based sintered material according to the present invention, a green body obtained by pressure forming raw material powder is sintered using a roller hearth furnace (continuous sintering furnace).
そのローラハース炉を用いて原料粉末の成形体を焼結温度に加熱した後、８３０℃〜９００℃まで冷却し、その後、２．５℃／ｓｅｃ〜４．０℃／ｓｅｃの速度で急冷する方法を採る。 A method in which a compact of raw material powder is heated to a sintering temperature using the roller hearth furnace, then cooled to 830 ° C. to 900 ° C., and then rapidly cooled at a rate of 2.5 ° C./sec to 4.0 ° C./sec. Take.
その方法の実施に用いるローラハース炉の一形態を図１及び図２に示す。このローラハース炉は、脱ガスゾーン１、予熱ゾーン２、加熱ゾーン３、冷却ゾーン４を順番に連ならせて構成されている。５は排ガス燃焼炉であり、脱ガスゾーン１において発生した排ガスがこの排ガス燃焼炉５に導入されて処理される。 One embodiment of a roller hearth furnace used for carrying out the method is shown in FIGS. This roller hearth furnace is configured by sequentially connecting a degassing zone 1, a preheating zone 2, a heating zone 3, and a cooling zone 4. Reference numeral 5 denotes an exhaust gas combustion furnace, and the exhaust gas generated in the degassing zone 1 is introduced into the exhaust gas combustion furnace 5 and processed.
加熱ゾーン３は、焼結室３ａとその焼結室３ａの後方に配置された徐冷室３ｂとからなる。 The heating zone 3 includes a sintering chamber 3a and a slow cooling chamber 3b arranged behind the sintering chamber 3a.
また、冷却ゾーン４は、急冷室４ａ、冷却室４ｂを組み合わせたものになっている。急冷室４ａと冷却室４ｂにおける冷却は窒素ガスを用いて行われる。 The cooling zone 4 is a combination of the quenching chamber 4a and the cooling chamber 4b. Cooling in the quenching chamber 4a and the cooling chamber 4b is performed using nitrogen gas.
設備の最後段の６は、窒素ガスと大気を置換する置換室である。この置換室６は、炉内に大気が流入するのを防止する目的で設けられている。 The last stage 6 of the facility is a replacement chamber for replacing nitrogen gas with the atmosphere. The replacement chamber 6 is provided for the purpose of preventing air from flowing into the furnace.
各ゾーンの内部には、動力駆動の送りローラ７が設けられており、その送りローラ７によってワークを収容したトレイＴが炉の上流から下流に向けて搬送される。 Inside each zone, a power-driven feed roller 7 is provided, and the feed roller 7 transports a tray T containing workpieces from upstream to downstream of the furnace.
徐冷室３ｂの入口と出口には、焼結室３ａとの間及び冷却ゾーン４との間を開閉可能に仕切る扉８、９がそれぞれ設けられている。また、急冷室４ａの入口と出口にも出入り口を開閉する扉１０，１１が設けられ、さらに、置換室６の入口部と出口部にも出入り口を開閉する扉１２，１３が設けられている。 Doors 8 and 9 are provided at the inlet and the outlet of the slow cooling chamber 3b so as to be openable and closable between the sintering chamber 3a and the cooling zone 4, respectively. Further, doors 10 and 11 for opening and closing the entrance and exit of the quenching chamber 4a are provided, and doors 12 and 13 for opening and closing the entrance and exit of the replacement chamber 6 are also provided.
冷却室４ｂの入口は急冷室４ａの出口に、また、冷却室４ｂの出口は置換室６の入口にそれぞれ連なっており、従って、冷却室４ｂの出入り口も、急冷室４ａの出口の扉１１と置換室６の入口の扉１２によって開閉されるようになっている。 The inlet of the cooling chamber 4b is connected to the outlet of the quenching chamber 4a, and the outlet of the cooling chamber 4b is connected to the inlet of the replacement chamber 6. Therefore, the inlet / outlet of the cooling chamber 4b is also connected to the outlet door 11 of the quenching chamber 4a. It is opened and closed by a door 12 at the entrance of the replacement chamber 6.
焼結炉の内部に設けた送りローラ７は、速度調整が可能な可変ローラである。冷却ゾーン４の内部に設けられた送りローラ７の搬送速度は、加熱ゾーン３における搬送速度よりも大に設定されている。 The feed roller 7 provided inside the sintering furnace is a variable roller capable of adjusting the speed. The conveying speed of the feed roller 7 provided in the cooling zone 4 is set to be higher than the conveying speed in the heating zone 3.
図１の１４はヒータ、図２の１５は急冷室用の冷却ファン、図１の１６はガスクーラ、１７は冷却室用の冷却ファン、１８は搬送コンベヤである。 In FIG. 1, 14 is a heater, 15 is a cooling fan for the quenching chamber, 16 is a gas cooler, 17 is a cooling fan for the cooling chamber, and 18 is a conveyor.
例示の炉では、徐冷室出口の扉９から急冷室入口の扉１０までの区間を高速で搬送することでワークの温度低下の抑制と、急冷室の温度上昇の防止を図っている。２℃／ｓｅｃ以上の冷却速度を得るための急冷室４ａから急冷室４ａ以降の長手方向中間点までの搬送速度は、徐冷室３ｂや急冷室４ａの長さ、徐冷室３ｂと急冷室４ａ間の長さ、急冷室４ａにおける冷却能力などによって変動する。 In the illustrated furnace, a section from the slow cooling chamber outlet door 9 to the quenching chamber inlet door 10 is conveyed at a high speed to suppress a decrease in the temperature of the workpiece and to prevent an increase in the temperature of the rapid cooling chamber. The conveying speed from the quenching chamber 4a for obtaining a cooling rate of 2 ° C./sec or more to the longitudinal intermediate point after the quenching chamber 4a is the length of the slow cooling chamber 3b or the quenching chamber 4a, the slow cooling chamber 3b and the quenching chamber. It varies depending on the length between 4a and the cooling capacity in the quenching chamber 4a.
排ガス燃焼炉５の入口から徐冷室３ｂまでの区間に設けられる送りローラ７の搬送速度は、同一に設定されている。 The conveyance speed of the feed roller 7 provided in the section from the inlet of the exhaust gas combustion furnace 5 to the slow cooling chamber 3b is set to be the same.
この発明の方法で製造する焼結材料は、Ｃｕの含有率が３．０ｗｔ％以下（０は除く）〜、Ｃの含有率が０．２〜１．０ｗｔ％、残Ｆｅの組成とする。 The sintered material produced by the method of the present invention has a Cu content of 3.0 wt% or less (excluding 0) to C, a C content of 0.2 to 1.0 wt%, and a residual Fe composition.
その組成の原料粉末で形成された成形体（ワーク）を収容したトレイＴを搬送ローラ７に載せてローラハース炉内に導入し、脱ガスゾーン１での脱ガス処理後に予熱ゾーン２を通過させてここでワークを７００℃〜９００℃程度に加熱する。 A tray T containing a molded body (work) formed of the raw material powder having the composition is placed on the conveying roller 7 and introduced into the roller hearth furnace, and after the degassing process in the degassing zone 1, it passes through the preheating zone 2. Here, the workpiece is heated to about 700 ° C to 900 ° C.
その後、トレイＴを焼結室３ａに導入してここでワークを焼結に必要な温度、例えば、１１３０℃程度の温度になるまで加熱し、その温度を所定時間保持して焼結を進める。 Thereafter, the tray T is introduced into the sintering chamber 3a, where the workpiece is heated to a temperature required for sintering, for example, about 1130 ° C., and the temperature is maintained for a predetermined time to advance the sintering.
焼結を終えたワークはトレイＴとともに徐冷室３ｂに導入してここで８３０〜９００℃の変態点直上まで冷却し、急冷室４ａの入口の扉１０が開かれるまで、その温度を保持して待機させる。このとき、扉８、９は閉じられている。 The sintered workpiece is introduced into the slow cooling chamber 3b together with the tray T and cooled to just above the transformation point of 830 to 900 ° C., and the temperature is maintained until the entrance door 10 of the quenching chamber 4a is opened. And wait. At this time, the doors 8 and 9 are closed.
先行するトレイＴが急冷室４ａでの冷却処理を終えて冷却室４ｂに送り出されると、扉１１が閉じられ、扉９，１０が開かれて徐冷室３ｂから急冷室４ａにトレイＴが送り込まれる。ここでの搬送速度は温度低下が焼入れに影響の無い小さな範囲に抑えられように設定される。 When the preceding tray T finishes the cooling process in the quenching chamber 4a and is sent to the cooling chamber 4b, the door 11 is closed, the doors 9 and 10 are opened, and the tray T is sent from the slow cooling chamber 3b to the quenching chamber 4a. It is. The conveyance speed here is set so that the temperature drop is suppressed to a small range that does not affect the quenching.
急冷室４ａ内ではトレイＴ内のワークに対して窒素ガスが吹きつけられ、それによって焼結後のワークが急速に冷却されて焼入れされる。その冷却は、２℃／ｓｅｃ以上の速度でなされる。冷却速度の上限は特に無いが、現状設備では４℃／ｓｅｃ程度が限界である。 In the quenching chamber 4a, nitrogen gas is blown against the workpiece in the tray T, whereby the sintered workpiece is rapidly cooled and quenched. The cooling is performed at a rate of 2 ° C./sec or more. Although there is no particular upper limit on the cooling rate, the current equipment has a limit of about 4 ° C./sec.
急冷室４ａを通過したワークは、トレイＴとともに冷却室４ｂに移されて３００℃を下回る温度になるまで冷却され、さらに、冷却室４ｂから置換室６に向けて搬送され、その間に酸化が起きない温度（２００℃以下、より好ましくは１５０℃以下）まで冷却されて出炉する。 The workpiece that has passed through the quenching chamber 4a is transferred to the cooling chamber 4b together with the tray T, cooled to a temperature lower than 300 ° C., and further conveyed from the cooling chamber 4b toward the replacement chamber 6, during which oxidation occurs. The furnace is cooled to a low temperature (200 ° C. or lower, more preferably 150 ° C. or lower).
かかる方法における炉内各部でのワーク温度の変動状況を図３に示す。この図３は、急冷室４ａでの冷却速度を３℃／ｓｅｃに設定したときの温度変化状況を示したものである。 The fluctuation | variation state of the workpiece | work temperature in each part in a furnace in this method is shown in FIG. FIG. 3 shows a temperature change state when the cooling rate in the quenching chamber 4a is set to 3 ° C./sec.
この発明の方法によれば、焼結後の急冷によって、フェライトと、パーライト中のセメンタイト相の析出間隔が５００ｎｍ以下の微細パーライトとが混在した組織を有する焼結材料が得られる。合金元素であるＣｕ及びＣの添加量の割りに冷却速度が小さいため、マルテンサイトは形成されない。 According to the method of the present invention, a sintered material having a structure in which ferrite and fine pearlite having a cementite phase precipitation interval of 500 nm or less are mixed by rapid cooling after sintering. Since the cooling rate is small relative to the addition amounts of Cu and C, which are alloy elements, martensite is not formed.
試作材料の組織を観察した結果、パーライト中のセメンタイト相の析出間隔が５００ｎｍ以下であったので、これを微細パーライトと定義した。 As a result of observing the structure of the prototype material, the precipitation interval of the cementite phase in pearlite was 500 nm or less, and this was defined as fine pearlite.
その材料の光学顕微鏡による組織写真を図４に示す。また、比較のために、フェライトとパーライトで構成されるＦｅ−Ｃｕ−Ｃ系焼結材料（通常材）の光学顕微鏡による組織写真を図５に示す。図４のＳＨは、急冷によりシンターハードニング実施品を示す（以下も同様）。 FIG. 4 shows a structure photograph of the material by an optical microscope. For comparison, FIG. 5 shows a structure photograph of an Fe—Cu—C based sintered material (ordinary material) composed of ferrite and pearlite by an optical microscope. SH in FIG. 4 shows a product subjected to sinter hardening by rapid cooling (the same applies to the following).
図４、図５の組織は、どちらもフェライトとパーライトで構成されている。図５の通常材では、パーライト部分がフェライトとセメンタイトの２相で構成されているのが顕微鏡写真で確認できる。 4 and 5 are both composed of ferrite and pearlite. In the normal material of FIG. 5, it can be confirmed from the micrograph that the pearlite portion is composed of two phases of ferrite and cementite.
一方、図４の材料は、パーライト中のフェライト相とセメンタイト相の間隔が微細であるため、暗い灰色として観察される。 On the other hand, the material of FIG. 4 is observed as dark gray because the interval between the ferrite phase and the cementite phase in pearlite is fine.
シンターハードニングでの冷却速度０．５℃／ｓｅｃの条件で製造される従来の同一組成の焼結材料（通常材）は、パーライト中のセメンタイト相の析出間隔が５００ｎｍ〜数μｍであるのに対し、この発明で言う微細パーライトはパーライト中のセメンタイト相の析出間隔が極めて小さい。 A conventional sintered material (usually material) having the same composition manufactured under conditions of a cooling rate of 0.5 ° C./sec in sintering hardening has a precipitation interval of cementite phase in pearlite of 500 nm to several μm. On the other hand, the fine pearlite referred to in the present invention has a very small precipitation interval of the cementite phase in the pearlite.
冷却速度の上昇によってセメンタイト（Ｆｅ３Ｃ）、フェライト（Ｆｅ）の核生成頻度が上昇し、その結果、それら２相の間隔が狭くなり、微細パーライトが形成される。そのセメンタイト相の析出間隔が狭い微細パーライトは、硬度が高く、焼結材の硬度、強度、耐摩耗性が改善される。 As the cooling rate increases, the frequency of nucleation of cementite (Fe 3 C) and ferrite (Fe) increases, and as a result, the interval between these two phases becomes narrower and fine pearlite is formed. Fine pearlite having a narrow cementite phase precipitation interval has high hardness, and the hardness, strength, and wear resistance of the sintered material are improved.
Ｆｅ−２ｗｔ％Ｃｕ−０．８ｗｔ％Ｃの組成の原料粉末を使用して密度６．６ｇ／ｃｍ３、６．８ｇ／ｃｍ３、及び７．０ｇ／ｃｍ３の粉末の成形体を作り、これをローラハース炉を使用して１１３０℃、２０分加熱の条件で焼結した。 Using a raw material powder having a composition of Fe-2 wt% Cu-0.8 wt% C, powder compacts having a density of 6.6 g / cm 3 , 6.8 g / cm 3 , and 7.0 g / cm 3 were prepared. This was sintered using a roller hearth furnace at 1130 ° C. for 20 minutes.
そして、その焼結工程において徐冷室での冷却後に急冷室において冷却速度３℃／ｓｅｃで急冷するシンターハードニング（ＳＨ）処理を行った。 And in the sintering process, the sintering hardening (SH) process which quenches rapidly with the cooling rate of 3 degree-C / sec in the quenching chamber after cooling in a slow cooling chamber .
次に、こうして作られた焼結材料の硬度、強度、耐摩耗性を評価した。その結果、密度６．８ｇ／ｃｍ３の材料については硬さが７５ＨＲＢ以上、外径：φ３４ｍｍ、内径：φ２０．２ｍｍ、厚み：１０ｍｍの試験片のＪＩＳ Ｚ ２５０７に準じた試験における圧環強度が９００ＭＰａ以上の測定値が得られた。図４の写真は、その６．８ｇ／ｃｍ３の焼結材料の組織である。 Next, the hardness, strength, and wear resistance of the sintered material thus produced were evaluated. As a result, for materials with a density of 6.8 g / cm 3 , the crushing strength in a test according to JIS Z 2507 of a test piece having a hardness of 75 HRB or more, an outer diameter: φ34 mm, an inner diameter: φ20.2 mm, and a thickness: 10 mm is 900 MPa. The above measured values were obtained. The photograph of FIG. 4 shows the structure of the sintered material of 6.8 g / cm 3 .
密度６．６ｇ／ｃｍ３の焼結材料の硬さは７５ＨＲＢ程度、密度６．８ｇ／ｃｍ３の焼結材料の硬さは７７ＨＲＢ程度、密度７．０ｇ／ｃｍ３の焼結材料の硬さは８５ＨＲＢに近い値が得られた。その硬さの測定結果を通常材の硬さと比較して図６に示す。 The hardness of the sintered material with a density of 6.6 g / cm 3 is about 75 HRB, the hardness of the sintered material with a density of 6.8 g / cm 3 is about 77 HRB, and the hardness of the sintered material with a density of 7.0 g / cm 3 A value close to 85 HRB was obtained. The measurement result of the hardness is shown in FIG. 6 in comparison with the hardness of a normal material.
材料の硬さは、ＪＩＳ Ｇ ０２０２に規定されたロックウェル試験によって求めた。 The hardness of the material was determined by the Rockwell test specified in JIS G0202.
また、密度６．８ｇ／ｃｍ３の材料の圧環強度の測定結果を、通常材の圧環強度と比較して図７に示す。 Moreover, the measurement result of the crushing strength of a material having a density of 6.8 g / cm 3 is shown in FIG. 7 in comparison with the crushing strength of a normal material.
この圧環強度は、ＪＩＳ Ｚ ２５０７に準じた圧環強度試験を行なって求めた。その圧環強度試験は、外径：φ３４ｍｍ、内径：φ２０．２ｍｍ、厚み：１０ｍｍの試験片を試験機｛（株）東京試験機製作所製｝に径方向に圧力を受けるようにセットし、下記の試験条件にて実施した。
試験条件：最大荷重を４０ｋＮに設定し、１．０［ＦＳ／ｍｉｎ］の定速試験力制御にて加圧。
The crushing strength was obtained by performing a crushing strength test according to JIS Z 2507. In the crushing strength test, a test piece having an outer diameter: φ34 mm, an inner diameter: φ20.2 mm, and a thickness: 10 mm was set on a tester {manufactured by Tokyo Test Machine Co., Ltd.} so as to receive pressure in the radial direction. The test was conducted under the test conditions.
Test conditions: The maximum load is set to 40 kN and pressurization is performed with constant speed test force control of 1.0 [FS / min].
さらに、摩耗試験による摩耗量の測定結果を、通常材の摩耗量と比較して図８に示す。この試験も密度６．８ｇ／ｃｍ３の焼結材を使用して行った。 Further, the measurement result of the wear amount by the wear test is shown in FIG. 8 in comparison with the wear amount of the normal material. This test was also performed using a sintered material having a density of 6.8 g / cm 3 .
この摩耗試験は、大越式摩耗試験機｛（株）東京試験機製作所製｝を使用して行った。
試験条件は、 相手材：ＳＣＭ４３５
摩擦速度：３．８１ｍ／ｓｅｃ
摩擦距離：２００ｍ
最終荷重：６．３ｋｇ
この条件で試験を行なった後に、試料の摩耗量を下記の近似式（１）を用いて摩耗による損失体積を求めて評価した。
摩耗量Ｗｍｍ３＝Ｂ×ｂ３÷（１２ｒ）・・・・・式（１）
ここに Ｂ：相手材厚み（３ｍｍ）
ｒ：相手材半径（１５ｍｍ）
ｂ：摩耗幅（実測値）
This wear test was performed using an Ogoshi type wear tester {manufactured by Tokyo Test Machine Co., Ltd.}.
Test conditions are: Opponent material: SCM435
Friction speed: 3.81 m / sec
Friction distance: 200m
Final load: 6.3kg
After performing the test under these conditions, the amount of wear of the sample was evaluated by determining the loss volume due to wear using the following approximate expression (1).
Wear amount Wmm 3 = B × b 3 ÷ (12r) Equation (1)
Here B: thickness of the mating material (3mm)
r: radius of the mating material (15mm)
b: Wear width (actual measured value)
図６の試験結果からわかるように、この発明の方法で製造されたＦｅ−Ｃｕ−Ｃ系焼結材料は、通常材に比べて１０ポイント程度硬さが増している。 As can be seen from the test results in FIG. 6, the Fe—Cu—C-based sintered material produced by the method of the present invention has increased in hardness by about 10 points compared to the normal material.
また、図７からわかるように、圧環強度は、通常材が８００ＭＰａ強であるのに対し、この発明の方法で製造された焼結材料は９５０ＭＰａ以上となっており、通常材に比べて
摩耗量も図８の通りに減少している。
Further, as can be seen from FIG. 7, the crushing strength of the normal material is over 800 MPa, whereas the sintered material manufactured by the method of the present invention is 950 MPa or more, which is the amount of wear compared to the normal material. As shown in FIG.
１ 脱ガスゾーン
２ 予熱ゾーン
３ 加熱ゾーン
３ａ 焼結室
３ｂ 徐冷室
４ 冷却ゾーン
４ａ 急冷室
４ｂ 冷却室
５ 排ガス燃焼炉
６ 置換室
７ 送りローラ
８〜１３ 扉
１４ ヒータ
１５、１７ 冷却ファン
１６ ガスクーラ
１８ 搬送コンベヤ
Ｔ トレイ
DESCRIPTION OF SYMBOLS 1 Degassing zone 2 Preheating zone 3 Heating zone 3a Sintering chamber 3b Slow cooling chamber 4 Cooling zone 4a Quenching chamber 4b Cooling chamber 5 Exhaust gas combustion furnace 6 Replacement chamber 7 Feed roller 8-13 Door 14 Heater 15, 17 Cooling fan 16 Gas cooler 18 Conveyor T
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