JP2014005543A - Iron-based powder mixture - Google Patents
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- JP2014005543A JP2014005543A JP2013170167A JP2013170167A JP2014005543A JP 2014005543 A JP2014005543 A JP 2014005543A JP 2013170167 A JP2013170167 A JP 2013170167A JP 2013170167 A JP2013170167 A JP 2013170167A JP 2014005543 A JP2014005543 A JP 2014005543A
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 156
- 239000000843 powder Substances 0.000 title claims abstract description 134
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 75
- 239000000203 mixture Substances 0.000 title claims abstract description 52
- 239000000654 additive Substances 0.000 claims abstract description 23
- 229910052751 metal Inorganic materials 0.000 claims abstract description 12
- 239000002184 metal Substances 0.000 claims abstract description 12
- 239000000344 soap Substances 0.000 claims abstract description 11
- 230000000996 additive effect Effects 0.000 claims abstract description 8
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 claims abstract description 6
- 229910045601 alloy Inorganic materials 0.000 claims description 19
- 239000000956 alloy Substances 0.000 claims description 19
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 4
- 238000005245 sintering Methods 0.000 abstract description 19
- 238000004663 powder metallurgy Methods 0.000 abstract description 7
- 230000002411 adverse Effects 0.000 abstract description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 17
- 238000005520 cutting process Methods 0.000 description 17
- 238000010438 heat treatment Methods 0.000 description 16
- 238000000465 moulding Methods 0.000 description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 14
- 239000010949 copper Substances 0.000 description 13
- 230000000694 effects Effects 0.000 description 12
- 238000002156 mixing Methods 0.000 description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 12
- 239000002245 particle Substances 0.000 description 11
- 238000004519 manufacturing process Methods 0.000 description 10
- 238000000034 method Methods 0.000 description 10
- 229910000831 Steel Inorganic materials 0.000 description 8
- 239000010959 steel Substances 0.000 description 8
- 238000005255 carburizing Methods 0.000 description 6
- 239000000314 lubricant Substances 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000003756 stirring Methods 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000010304 firing Methods 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910021382 natural graphite Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000004033 plastic Substances 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 235000008708 Morus alba Nutrition 0.000 description 1
- 240000000249 Morus alba Species 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- CEGOLXSVJUTHNZ-UHFFFAOYSA-K aluminium tristearate Chemical compound [Al+3].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O CEGOLXSVJUTHNZ-UHFFFAOYSA-K 0.000 description 1
- 229940063655 aluminum stearate Drugs 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- TZCXTZWJZNENPQ-UHFFFAOYSA-L barium sulfate Chemical compound [Ba+2].[O-]S([O-])(=O)=O TZCXTZWJZNENPQ-UHFFFAOYSA-L 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000005256 carbonitriding Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000011195 cermet Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- BERDEBHAJNAUOM-UHFFFAOYSA-N copper(I) oxide Inorganic materials [Cu]O[Cu] BERDEBHAJNAUOM-UHFFFAOYSA-N 0.000 description 1
- KRFJLUBVMFXRPN-UHFFFAOYSA-N cuprous oxide Chemical compound [O-2].[Cu+].[Cu+] KRFJLUBVMFXRPN-UHFFFAOYSA-N 0.000 description 1
- 229940112669 cuprous oxide Drugs 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- UQLDLKMNUJERMK-UHFFFAOYSA-L di(octadecanoyloxy)lead Chemical compound [Pb+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O UQLDLKMNUJERMK-UHFFFAOYSA-L 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- FPAFDBFIGPHWGO-UHFFFAOYSA-N dioxosilane;oxomagnesium;hydrate Chemical compound O.[Mg]=O.[Mg]=O.[Mg]=O.O=[Si]=O.O=[Si]=O.O=[Si]=O.O=[Si]=O FPAFDBFIGPHWGO-UHFFFAOYSA-N 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- NBVXSUQYWXRMNV-UHFFFAOYSA-N fluoromethane Chemical compound FC NBVXSUQYWXRMNV-UHFFFAOYSA-N 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910000040 hydrogen fluoride Inorganic materials 0.000 description 1
- 150000002484 inorganic compounds Chemical class 0.000 description 1
- 229910010272 inorganic material Inorganic materials 0.000 description 1
- VAKIVKMUBMZANL-UHFFFAOYSA-N iron phosphide Chemical compound P.[Fe].[Fe].[Fe] VAKIVKMUBMZANL-UHFFFAOYSA-N 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- HGPXWXLYXNVULB-UHFFFAOYSA-M lithium stearate Chemical compound [Li+].CCCCCCCCCCCCCCCCCC([O-])=O HGPXWXLYXNVULB-UHFFFAOYSA-M 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000008707 rearrangement Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- TXEYQDLBPFQVAA-UHFFFAOYSA-N tetrafluoromethane Chemical compound FC(F)(F)F TXEYQDLBPFQVAA-UHFFFAOYSA-N 0.000 description 1
Abstract
Description
本発明は、鉄粉、合金鋼粉などの鉄基粉末に、所定の添加材、さらには黒鉛粉および銅粉などの合金用粉末を混合した鉄基粉末混合物に関し、さらに詳しくは、常温から100℃未満の温度域での加圧成形において優れた圧縮性が得られ、特に自動車用高強度焼結部品の製造に好適な粉末冶金用の鉄基粉末混合物に関するものである。 The present invention relates to an iron-based powder mixture in which iron-based powders such as iron powder and alloy steel powder are mixed with predetermined additives, and further alloy powders such as graphite powder and copper powder. The present invention relates to an iron-based powder mixture for powder metallurgy, which is excellent in compressibility in pressure molding in a temperature range of less than 0 ° C. and is particularly suitable for the production of high-strength sintered parts for automobiles.
粉末冶金用の鉄基粉末混合物は、鉄基粉末に、銅粉や黒鉛粉、燐化鉄粉などの合金用粉末と、ステアリン酸亜鉛やステアリン酸アルミニウム、ステアリン酸鉛などの潤滑剤、さらに必要に応じて切削性改善用粉末を混合して製造するのが一般的である。そして、使用する潤滑剤は、鉄基粉末との混合性や焼結時の散逸性などを考慮して選択されてきた。 Iron-based powder mixture for powder metallurgy requires iron-based powder, alloy powder such as copper powder, graphite powder and iron phosphide powder, lubricant such as zinc stearate, aluminum stearate and lead stearate, and more In general, it is generally produced by mixing the machinability improving powder. The lubricant to be used has been selected in consideration of the miscibility with the iron-based powder and the dissipating property during sintering.
近年、焼結部品に対する高強度化の要求の高まりと共に、特許文献１、特許文献２、特許文献３および特許文献４に開示されたように、鉄基粉末混合物を加熱しつつ成形することにより、成形体の高密度かつ高強度化を可能にする温間成形技術が開発された。この技術により、鉄基粉末が加熱により塑性変形抵抗が低下することを利用して、より低い荷重での成形体密度の向上が可能となった。 In recent years, with increasing demand for higher strength for sintered parts, as disclosed in Patent Document 1, Patent Document 2, Patent Document 3 and Patent Document 4, by molding an iron-based powder mixture while heating, Warm forming technology that enables high density and high strength of the compact has been developed. This technique makes it possible to improve the density of the molded body at a lower load by utilizing the fact that the plastic deformation resistance of iron-based powder is reduced by heating.
しかしながら、このような鉄基粉末混合物は、以下に述べるような問題を残していた。
すなわち、温間成形は、金型および粉末を100℃以上の高温に予め加熱した後、鉄基粉末混合物を加圧成形する技術であるが、熱伝導性が悪い鉄基粉末混合物を安定して100℃以上に加熱・保温することは極めて難しいため、焼結部品の生産性の低下を招く傾向にあった。また、鉄基粉末混合物を長時間加熱することによって、鉄基粉末混合物の酸化による変質という問題も生じていた。
However, such an iron-based powder mixture has left the following problems.
In other words, warm molding is a technique in which a mold and powder are preheated to a high temperature of 100 ° C. or higher, and then an iron-based powder mixture is pressure-molded, but an iron-based powder mixture having poor thermal conductivity is stably formed. Since it is extremely difficult to heat and keep above 100 ° C., the productivity of sintered parts tends to be reduced. In addition, heating the iron-based powder mixture for a long time has caused a problem of alteration due to oxidation of the iron-based powder mixture.
また、特許文献５や特許文献６には、MoS2やフッ化炭素、黒鉛などの層状結晶を有する無機化合物を潤滑剤として用いる技術が開示されている。
しかしながら、MoS2を用いた場合は、焼結時に分解して有害なＳが発生し、焼成炉が汚染される危険性がある。また、フッ化炭素を用い、水素雰囲気中で焼結した場合は、フッ化水素の発生が懸念される。
Patent Documents 5 and 6 disclose techniques using an inorganic compound having a layered crystal such as MoS 2 , fluorocarbon, and graphite as a lubricant.
However, when MoS 2 is used, there is a risk of decomposing at the time of sintering, generating harmful S and contaminating the firing furnace. In addition, when carbon fluoride is used and sintered in a hydrogen atmosphere, the generation of hydrogen fluoride is a concern.
ところで、自動車等の各種機械の部品を粉末冶金技術で製造するには、鉄基粉末混合物を金型に充填して圧粉成形し、さらに焼結を行う。こうして得られた焼結部品は寸法精度が良く、複雑な形状のものを製造することができる。但し、非常に厳しい寸法精度が要求される焼結部品を製造する場合には、焼結した後に、さらに機械加工（例えば切削加工やドリル加工等）を施す必要がある。 By the way, in order to manufacture parts of various machines such as automobiles by powder metallurgy technology, an iron-based powder mixture is filled in a mold, compacted, and further sintered. The sintered parts thus obtained have good dimensional accuracy and can be manufactured in complex shapes. However, when manufacturing a sintered part that requires extremely strict dimensional accuracy, it is necessary to perform further machining (for example, cutting or drilling) after sintering.
しかしながら、焼結部品は切削性に劣るので、機械加工で使用する切削工具が著しく損耗する。その結果、機械加工費が増大し、焼結部品の製造コストの上昇を招く。このような焼結部品の切削性の劣化は、内部に存在する気孔によって焼結部品の熱伝導率が低下し、切削中の焼結部品の温度が上昇するために生じる。 However, since sintered parts are inferior in machinability, cutting tools used in machining are significantly worn. As a result, the machining cost increases and the manufacturing cost of the sintered part increases. Such deterioration of the machinability of the sintered part is caused by a decrease in the thermal conductivity of the sintered part due to pores present inside, and an increase in the temperature of the sintered part during cutting.
粉末冶金用の鉄基粉末混合物に快削成分（例えばＳ、MnＳ等）を添加することによって、焼結部品の切削性が改善されることは従来から知られている。快削成分は、切り屑を容易に破断させる効果、あるいは切削工具に薄い構成刃先を形成して切削工具（特にすくい面）の潤滑性を高める効果を有している。 It has been conventionally known that the machinability of sintered parts is improved by adding a free-cutting component (for example, S, MnS, etc.) to an iron-based powder mixture for powder metallurgy. The free-cutting component has the effect of easily breaking chips, or the effect of increasing the lubricity of a cutting tool (particularly the rake face) by forming a thin component edge on the cutting tool.
焼結部品は、様々な機器の部品として採用されているが、とりわけ自動車の部品（例えばギヤ等）は高強度、高疲労強度が要求される。そこで、高強度、高疲労強度を有する焼結部品を製造するために、合金成分を添加した鉄基粉末混合物を使用する技術が種々検討されている。
例えば、特許文献７には、Ni，Cu，Mo等の粉末を純鉄粉に付着拡散させる技術が開示されている。この技術で得られた鉄基粉末混合物は圧縮性に優れており、高強度、高疲労強度を有する焼結部品の製造に好適である。
しかしながら、特許文献７に開示された技術では、Niの拡散が遅いので、純鉄粉にNiを十分に拡散させるために長時間の焼結が必要となる。また、得られた焼結部品の硬度が高いので、快削成分を鉄基粉末混合物に添加しても切削性の大幅な改善は期待できない。
Sintered parts are used as parts for various devices, but automobile parts (for example, gears) are required to have high strength and high fatigue strength. Therefore, various techniques using an iron-based powder mixture to which alloy components are added have been studied in order to produce sintered parts having high strength and high fatigue strength.
For example, Patent Document 7 discloses a technique for adhering and diffusing powders such as Ni, Cu, and Mo to pure iron powder. The iron-based powder mixture obtained by this technique has excellent compressibility and is suitable for the production of sintered parts having high strength and high fatigue strength.
However, in the technique disclosed in Patent Document 7, since diffusion of Ni is slow, long-time sintering is required to sufficiently diffuse Ni into the pure iron powder. Moreover, since the hardness of the obtained sintered part is high, even if a free-cutting component is added to the iron-based powder mixture, a significant improvement in machinability cannot be expected.
また、引用文献８には、ＣとMoを含有し、MnとCrを実質的に含有しない低合金鋼粉に、Cu粉および／またはNi粉を添加し、さらに黒鉛粉を添加した鉄基粉末混合物が開示されている。さらに、引用文献９には、Mo，Mn，Ｃを含有する合金鋼粉にCu粉を融着させた鉄基粉末混合物が開示されている。これらの鉄基粉末混合物は、高強度の焼結部品の製造に好適である。
しかしながら、特許文献８，９に開示された鉄基粉末混合物では、切削性に優れた焼結部品を製造することは困難であった。
Also, in Cited Document 8, an iron-based powder in which Cu powder and / or Ni powder is added to a low alloy steel powder containing C and Mo but substantially free of Mn and Cr, and further graphite powder is added. Mixtures are disclosed. Furthermore, cited document 9 discloses an iron-based powder mixture in which Cu powder is fused to alloy steel powder containing Mo, Mn, and C. These iron-based powder mixtures are suitable for the production of high strength sintered parts.
However, with the iron-based powder mixture disclosed in Patent Documents 8 and 9, it was difficult to produce a sintered part excellent in machinability.
本発明は、上記の問題を有利に解決するもので、成形体の焼結に際し、焼成炉の炉内環境に悪影響を及ぼすことなく、また100℃未満という低温度域で優れた成形性が得られ、しかも切削性に優れた焼結部品を製造するのに好適な粉末冶金用の鉄基粉末混合物を提案することを目的とする。 The present invention advantageously solves the above-mentioned problems, and has excellent moldability in a low temperature range of less than 100 ° C. without adversely affecting the furnace environment of the firing furnace when the molded body is sintered. Another object of the present invention is to propose an iron-based powder mixture for powder metallurgy that is suitable for producing sintered parts excellent in machinability.
さて、発明者らは、上記の問題を解決する方策として、鉄基粉末混合物の成形に際し、炉内環境に悪影響を及ぼすことなく、また鉄基粉末混合物の加熱温度をより低く、好ましくは加熱なしに成形した場合であっても、高密度の成形体の製造を可能とする添加材について、鋭意検討を重ねた。
その結果、添加材として、ステアタイトならびに金属石鹸を用いた場合に、これらの添加材の潤滑機能により、加圧成形時に鉄基粉末粒子の再配列が促進され、室温程度の低い成形温度であっても、成形密度の高い鉄基粉末成形体が得られること、またかかる鉄基粉末成形体を焼結して得られる焼結体は機械的強度および切削性に優れていることの知見を得た。
本発明は上記の知見に立脚するものである。
Now, as a measure for solving the above problems, the inventors do not adversely affect the furnace environment when forming the iron-based powder mixture, and lower the heating temperature of the iron-based powder mixture, preferably no heating. Even in the case of forming into a compact, the inventors have made extensive studies on the additive that enables the production of a high-density molded body.
As a result, when steatite and metal soap are used as additives, the lubrication function of these additives promotes the rearrangement of iron-based powder particles during pressure molding, resulting in a molding temperature as low as room temperature. However, it has been found that an iron-based powder compact with a high molding density can be obtained, and that a sintered compact obtained by sintering such an iron-based powder compact has excellent mechanical strength and machinability. It was.
The present invention is based on the above findings.
すなわち、本発明の要旨構成は次のとおりである。
（１）鉄基粉末と、この鉄基粉末100mass％に対し、モル比：MgO/SiO2の値が１のステアタイト：0.01〜0.5mass％、および金属石鹸：0.1〜1.0mass％（但し、ステアリン酸亜鉛≦0.2mass％を除く）からなる添加材との組み合わせになることを特徴とする鉄基粉末混合物。
That is, the gist configuration of the present invention is as follows.
(1) With respect to iron-base powder and 100 mass% of this iron-base powder, the molar ratio: MgO / SiO 2 value of 1 steatite: 0.01 to 0.5 mass%, and metal soap: 0.1 to 1.0 mass% (however, An iron-based powder mixture characterized by being combined with an additive consisting of zinc stearate ≦ 0.2 mass%).
（２）前記鉄基粉末混合物中に、さらに合金用粉末を配合したことを特徴とする前記（１）に記載の鉄基粉末混合物。 (2) The iron-based powder mixture according to (1), wherein an alloy powder is further blended in the iron-based powder mixture.
本発明によれば、室温程度の低い温度で成形したとしても、成形密度が高くかつ抜出力が小さい鉄基粉末混合物を得ることができる。 According to this invention, even if it shape | molds at the low temperature of about room temperature, the iron-based powder mixture with a high shaping | molding density and a small extraction output can be obtained.
以下、本発明を具体的に説明する。
まず、本発明の鉄基粉末混合物の原料について説明する。
本発明において、鉄基粉末としては、アトマイズ鉄粉や還元鉄粉などの純鉄粉、または部分拡散合金化鋼粉および完全合金化鋼粉、さらには完全合金化鋼粉に合金成分を部分拡散させたハイブリッド鋼粉などが例示される。
Hereinafter, the present invention will be specifically described.
First, the raw material of the iron-based powder mixture of the present invention will be described.
In the present invention, as iron-based powder, pure iron powder such as atomized iron powder and reduced iron powder, or partially diffused alloyed steel powder and fully alloyed steel powder, and further partially diffused alloy components in fully alloyed steel powder. The hybrid steel powder etc. which were made to be illustrated are illustrated.
また、合金用粉末としては、黒鉛粉末、Cu，Mo，Niなどの金属粉末、ボロン粉末および亜酸化銅粉末などが例示される。これらの合金用粉末を鉄基粉末に混合させることにより焼結体の強度を上昇させることができる。
この合金用粉末の配合量は、鉄基粉末混合物中0.1〜10mass％程度とすることが好ましい。というのは、合金用粉末を0.1mass％以上配合することにより、得られる焼結体の強度が有利に向上し、一方10mass％を超えると焼結体の寸法精度が低下するからである。
Examples of the alloy powder include graphite powder, metal powder such as Cu, Mo, and Ni, boron powder, and cuprous oxide powder. The strength of the sintered body can be increased by mixing these alloy powders with the iron-based powder.
The blending amount of the alloy powder is preferably about 0.1 to 10 mass% in the iron-based powder mixture. This is because, by adding 0.1 mass% or more of the alloy powder, the strength of the obtained sintered body is advantageously improved, while when it exceeds 10 mass%, the dimensional accuracy of the sintered body decreases.
さて、本発明では、添加材として、ステアタイトと、金属石鹸とを添加することが重要である。そして、ステアタイトは単斜晶系の結晶構造を有することが好ましい。 In the present invention, it is important to add steatite and metal soap as additives. The steatite preferably has a monoclinic crystal structure.
添加材として、上記したステアタイトおよび金属石鹸を添加することにより、成形体の圧縮性が向上すると同時に、成形時の抜出力が低減し、成形性が大幅に改善される理由は、次のとおりと考えられる。
すなわち、ステアタイトは、成形時に鉄基粉末粒子間で剪断応力を受けた際に、上記物質が結晶面に沿ってへき開し易く、そのため成形体内部の粒子間の摩擦抵抗が低減し、粒子間相互で動き易くなるという潤滑効果によって、成形体の密度が向上するものと考えられる。また、成形体と金型間にステアタイトが存在すると、成形体抜出時に金型表面からの剪断応力を受けてへき開するため、金型表面での成形体のすべり易さが向上し、抜出力が低減するものと考えられる。なお、これらの効果は、さらに金属石鹸を添加することによって、格段に改善される。
By adding the above-mentioned steatite and metal soap as additives, the compressibility of the molded body is improved, and at the same time, the output during molding is reduced and the moldability is greatly improved. it is conceivable that.
That is, when the steatite is subjected to shear stress between the iron-based powder particles during molding, the substance is easily cleaved along the crystal plane, so that the friction resistance between the particles inside the compact is reduced, and the inter-particle It is considered that the density of the molded body is improved by the lubricating effect of facilitating mutual movement. In addition, if steatite is present between the molded body and the mold, it is cleaved due to the shear stress from the mold surface when the molded body is pulled out, which improves the ease of sliding of the molded body on the mold surface. The output is considered to be reduced. In addition, these effects are remarkably improved by adding metal soap.
これらの効果は、鉄基粉末混合物の温度によらず発現するため、鉄基粉末混合物を加熱する必要は必ずしもなく、常温での成形における鉄基粉末成形体の密度向上に有効に寄与する。また、鉄基粉末を加熱した場合は、加圧成形時に鉄基粉末の塑性変形抵抗が低下するため、より高い成形体密度が得られることが可能となる。従って、必要とする成形体密度に応じて、鉄基粉末の加熱温度を適宜設定することができるが、この加熱温度は100℃未満で十分である。 Since these effects are manifested regardless of the temperature of the iron-based powder mixture, it is not always necessary to heat the iron-based powder mixture, which effectively contributes to improving the density of the iron-based powder molded body in molding at room temperature. In addition, when the iron-based powder is heated, the plastic deformation resistance of the iron-based powder is reduced during pressure molding, so that a higher molded body density can be obtained. Therefore, although the heating temperature of the iron-based powder can be set as appropriate according to the required density of the compact, it is sufficient that the heating temperature is less than 100 ° C.
ステアタイトの添加量は、鉄基粉末混合物全体に対し0.01〜0.5mass％とする必要がある。というのは、これらの添加材を0.01mass％以上添加することにより、加圧成形時における成形体密度を十分に向上させ、かつ成形体抜出時における抜出力を十分に低減させることができるからである。一方、添加量が0.5mass％を超えると、成形体を焼結して得た焼結材の機械的強度を低下させることが懸念される。 The addition amount of steatite needs to be 0.01 to 0.5 mass% with respect to the entire iron-based powder mixture. This is because by adding 0.01 mass% or more of these additives, it is possible to sufficiently improve the density of the molded body at the time of pressure molding and sufficiently reduce the output at the time of extracting the molded body. It is. On the other hand, when the added amount exceeds 0.5 mass%, there is a concern that the mechanical strength of the sintered material obtained by sintering the compact is reduced.
また、金属石鹸としてはステアリン酸亜鉛およびステアリン酸リチウムなどが好ましい。これらは、前記成形時の潤滑効果により、粒子間の摩擦抵抗を低減し、粒子相互を動きやすくすることにより、成形体の密度を向上させるだけでなく、鉄基粉末混合物の流動性をさらに向上させることができる。
この金属石鹸の添加量は、鉄基粉末混合物全体に対し0.1〜1.0mass％（但し、ステアリン酸亜鉛≦0.2mass％を除く）とすることが好ましい。というのは、添加量が0.1mass％に満たないとその添加効果に乏しく、一方1.0mass％を超えると成形体の強度が低下するからである。
Further, as the metal soap, zinc stearate and lithium stearate are preferable. These not only improve the density of the compact but also improve the fluidity of the iron-based powder mixture by reducing the frictional resistance between the particles and making the particles easier to move due to the lubricating effect during the molding. Can be made.
The addition amount of the metal soap is preferably 0.1 to 1.0 mass% (excluding zinc stearate ≦ 0.2 mass%) with respect to the entire iron-based powder mixture. This is because if the addition amount is less than 0.1 mass%, the effect of the addition is poor, while if it exceeds 1.0 mass%, the strength of the molded article is lowered.
また、ステアタイトは、潤滑性能を発揮する他、鉄基粉末混合物を成形し、焼結する際に分解しない、すなわち有害な分解ガスを発生させず、焼結を阻害しないため、焼結体の機械的強度の向上にも寄与する。
さらに、ステアタイトは、快削成分として知られるMgO−SiO2系酸化物であり、焼結体の切削性の改善にも有効に寄与するが、その効果は金属石鹸と複合添加することにより一層向上する。
以下、上記の効果を発現させるのに好適なステアタイトの添加量について説明する。
Steatite not only exhibits lubrication performance, but also does not decompose when forming and sintering an iron-based powder mixture, that is, does not generate harmful decomposition gas and does not inhibit sintering. It contributes to the improvement of mechanical strength.
Furthermore, steatite is an MgO-SiO 2 oxide known as a free-cutting component, and contributes to the improvement of the machinability of the sintered body. improves.
Hereinafter, the amount of addition of steatite suitable for exhibiting the above effect will be described.
上記の目的でステアタイト（MgＯ・SiO2）を添加する場合、添加量が0.01mass％に満たないと十分に満足いくほどの切削性の改善効果が得られず、一方0.5mass％を超えると鉄基粉末混合物の圧縮性が低下し、焼結部品の強度低下を招く。
従って、特に好適な機械的強度および切削性を得ようとする場合にも、ステアタイトの添加は0.01〜0.5mass％の範囲とする必要がある。
When steatite (MgO · SiO 2 ) is added for the above purpose, if the addition amount is less than 0.01 mass%, the satisfactory machinability improvement effect cannot be obtained, while if it exceeds 0.5 mass% The compressibility of the iron-based powder mixture is reduced and the strength of the sintered part is reduced.
Therefore, also in order to obtain particularly suitable mechanical strength and machinability, the addition of steatite needs to be in the range of 0.01 to 0.5 mass%.
次に、上記した優れた機械的強度および切削性を得るのに好適な合金組成について説明する。
鉄基粉末としては、水アトマイズ合金鋼粉が好適であり、合金成分については次のとおりである。なお、合金成分の含有量（mass％）は、水アトマイズ合金鋼粉と後述する添加剤とを混合して得られる鉄基粉末混合物の質量（mass％）に占める比率を内数で示す。
Mo：0.3〜0.5mass％
Moは、水アトマイズ合金鋼粉の固溶強化、焼入れ性向上によって焼結部品の強度を高める元素である。しかしながら、含有量が0.3mass％未満では、十分満足いくほどの焼結部品の強度向上が望めず、一方0.5mass％を超えると、焼結部品の強度向上効果が飽和するばかりか、切削性の低下を招く。従って、Moは0.3〜0.5mass％の範囲内が好ましい。
Next, an alloy composition suitable for obtaining the above-described excellent mechanical strength and machinability will be described.
As the iron-based powder, water atomized alloy steel powder is suitable, and the alloy components are as follows. In addition, content (mass%) of an alloy component shows the ratio which occupies for the mass (mass%) of the iron-based powder mixture obtained by mixing water atomized alloy steel powder and the additive mentioned later by an internal number.
Mo: 0.3-0.5mass%
Mo is an element that enhances the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. However, if the content is less than 0.3 mass%, it is not possible to expect a sufficiently satisfactory improvement in the strength of the sintered part. On the other hand, if it exceeds 0.5 mass%, not only the strength improvement effect of the sintered part is saturated but also the machinability Incurs a decline. Therefore, Mo is preferably in the range of 0.3 to 0.5 mass%.
Mn：0.1〜0.25mass％
Mnも、水アトマイズ合金鋼粉の固溶強化、焼入れ性向上によって焼結部品の強度を高める元素である。しかしながら、含有量が0.1mass％未満では、やはり十分な焼結部品の強度向上が望めず、一方0.25mass％を超えると、Mnの酸化が進行し易くなり、合金鋼粉の強度と圧縮性が低下する。従って、Mnは0.1〜0.25mass％の範囲内が好ましい。
Mn: 0.1-0.25mass%
Mn is an element that enhances the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. However, if the content is less than 0.1 mass%, sufficient strength improvement of the sintered parts cannot be expected. On the other hand, if the content exceeds 0.25 mass%, the oxidation of Mn tends to proceed, and the strength and compressibility of the alloy steel powder are reduced. descend. Therefore, Mn is preferably in the range of 0.1 to 0.25 mass%.
上記した水アトマイズ合金鋼粉には、以下に述べる合金用粉末を混合することができる。なお、これらの合金用粉末の添加量（mass％）は、水アトマイズ合金鋼粉と合金用粉末とを混合して得られる鉄基粉末混合物の質量（mass％）に占める比率を内数で示す。
Cu粉：１〜３mass％
Cuは、水アトマイズ合金鋼粉の固溶強化、焼入れ性向上によって焼結部品の強度を高める元素である。また、Cu粉は、焼結の際に溶融して液相となり、水アトマイズ合金鋼粉の粒子を互いに固着させる作用がある。しかしながら、添加量が１mass％に満たないとその効果に乏しく、一方３mass％を超えると、焼結部品の強度向上効果が飽和するばかりでなく、切削性の低下を招く。従って、Cu粉は１〜３mass％の範囲内が好ましい。
The above-mentioned water atomized alloy steel powder can be mixed with an alloy powder described below. In addition, the addition amount (mass%) of these powders for alloys shows the ratio which occupies for the mass (mass%) of the iron-based powder mixture obtained by mixing water atomized alloy steel powder and the powder for alloys by an internal number. .
Cu powder: 1-3mass%
Cu is an element that increases the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. Further, the Cu powder melts during sintering to form a liquid phase, and has an effect of fixing the particles of the water atomized alloy steel powder to each other. However, if the added amount is less than 1 mass%, the effect is poor. On the other hand, if it exceeds 3 mass%, the effect of improving the strength of the sintered part is saturated, and the machinability is reduced. Therefore, the Cu powder is preferably in the range of 1 to 3 mass%.
なお、Cuを添加するにあたっては、添加量が上記の範囲内であれば、
(a) 水アトマイズ合金鋼粉にCu粉を添加して単に混合する、
(b) 水アトマイズ合金鋼粉の表面にバインダーを介してCu粉を付着させる、
(c) 水アトマイズ合金鋼粉とCu粉を混合し、さらに熱処理して水アトマイズ合金鋼粉の表面にCu粉を付着拡散させる
という方法のいずれを採用しても良い。
In addition, when adding Cu, if the addition amount is within the above range,
(a) Add Cu powder to water atomized alloy steel powder and simply mix.
(b) Adhering Cu powder to the surface of the water atomized alloy steel powder via a binder,
(c) Any of the methods of mixing water atomized alloy steel powder and Cu powder, further heat-treating, and adhering and diffusing Cu powder on the surface of the water atomized alloy steel powder may be adopted.
黒鉛粉：0.1〜1.0mass％
黒鉛粉の主成分であるＣは、焼鈍時に鉄に固溶し、固溶強化、焼入れ性向上によって焼結部品の強度を高める元素である。焼結後に浸炭熱処理等で、焼結体に外部から浸炭する場合には、添加する黒鉛粉は少なくてもよく、0.1mass％以上あればよい。一方、焼結後に浸炭熱処理しない場合には、黒鉛粉の含有量が0.5mass％未満ではその添加効果に乏しい。また、いずれの場合も、黒鉛粉の含有量が1.0mass％を超えると過共析になるためセメンタイトが析出し、強度が低下するだけでなく切削性の低下を招く。従って、黒鉛粉は0.1〜1.0mass％の範囲内とする。なお、焼結後に浸炭熱処理を行う場合でも、焼結体内部まではなかなか浸炭しないので、黒鉛粉は0.1〜0.7mass％程度含有させることが好ましい。
Graphite powder: 0.1-1.0mass%
C, which is the main component of the graphite powder, is an element that dissolves in iron during annealing and increases the strength of the sintered part by solid solution strengthening and hardenability improvement. When carburizing the sintered body from the outside by carburizing heat treatment or the like after sintering, the graphite powder to be added may be small and may be 0.1 mass% or more. On the other hand, when the carburizing heat treatment is not performed after sintering, the addition effect is poor when the content of the graphite powder is less than 0.5 mass%. Moreover, in any case, when the graphite powder content exceeds 1.0 mass%, hypereutectoid is formed, so that cementite is precipitated, not only the strength is lowered, but also the machinability is lowered. Therefore, the graphite powder is within the range of 0.1 to 1.0 mass%. In addition, even when carburizing heat treatment is performed after sintering, the inside of the sintered body is not easily carburized, so it is preferable to contain about 0.1 to 0.7 mass% of graphite powder.
次に、本発明の鉄基粉末混合物の製造方法について説明する。
鉄基粉末に、ステアタイトおよび金属石鹸などの添加材、さらに必要に応じて合金用粉末を加えて、１次混合する。ついで、１次混合後の混合物を、上記した添加材のうち少なくとも１種の添加材の融点以上に加熱しつつ撹拌し、混合しながら徐々に冷却して、鉄基粉末の表面に溶融した添加剤によって合金用粉末やその他の添加剤を固着させる。
なお、上記したステアタイト、金属石鹸などの添加材は、必ずしも全量を一度に添加する必要はなく、一部のみを添加して１次混合を行ったのち、残部を添加して２次混合することもできる。
また、混合手段としては、特に制限はなく従来から公知の混合機いずれもが使用できるが、加熱が容易な、高速底部撹拌式混合機、傾斜回転パン型混合機、回転クワ型混合機および円錐遊星スクリュー形混合機などは特に有利に適合する。
Next, the manufacturing method of the iron-based powder mixture of this invention is demonstrated.
Additives such as steatite and metal soap, and, if necessary, alloy powder are added to the iron-based powder, followed by primary mixing. Next, the mixture after the primary mixing is stirred while being heated above the melting point of at least one of the above-mentioned additives, gradually cooled while mixing, and added to the surface of the iron-based powder. The alloy powder and other additives are fixed by the agent.
In addition, it is not always necessary to add the total amount of the above-described additives such as steatite and metal soap, but after adding only a part and performing primary mixing, the remainder is added and secondarily mixed. You can also.
The mixing means is not particularly limited and any conventionally known mixer can be used. However, a high-speed bottom stirring mixer, an inclined rotary pan mixer, a rotary mulberry mixer, and a cone that can be easily heated can be used. A planetary screw type mixer or the like is particularly advantageously adapted.
次に、本発明の鉄基粉末混合物を用いた鉄基粉末成形体の製造方法および鉄基粉末焼結体の製造方法について説明する。
本発明の鉄基粉末混合物は、通常の成形方法で成形体とすることができる。すなわち、常温で成形することができる。とはいえ、鉄基粉末混合物や金型を加熱したり、金型に潤滑剤を塗布することは有利である。加熱雰囲気で成形を行う場合、鉄基粉末混合物や金型の温度は100℃未満とすることが好ましい。というのは、本発明に従う鉄基粉末混合物は圧縮性に富むので100℃未満の温度でも優れた成形性を示し、また100℃以上になると酸化による劣化が懸念されるからである。
Next, a method for producing an iron-based powder molded body and a method for producing an iron-based powder sintered body using the iron-based powder mixture of the present invention will be described.
The iron-based powder mixture of the present invention can be formed into a molded body by a normal molding method. That is, it can be molded at room temperature. Nevertheless, it is advantageous to heat the iron-based powder mixture or the mold or to apply a lubricant to the mold. When molding is performed in a heated atmosphere, the temperature of the iron-based powder mixture and the mold is preferably less than 100 ° C. This is because the iron-based powder mixture according to the present invention is highly compressible and exhibits excellent moldability even at temperatures below 100 ° C., and when it exceeds 100 ° C., there is a concern about deterioration due to oxidation.
ついで、上記のようにして得られた高密度鉄基粉末成形体に、焼結処理を施して、高密度の焼結体とする。焼結処理については、特に限定されることはなく、従来公知の焼結処理方法いずれもが好適に使用できる。また、焼結処理後に、ガス浸炭熱処理や浸炭窒化処理等の熱処理を適用することも可能である。 Next, the high-density iron-based powder molded body obtained as described above is subjected to a sintering treatment to obtain a high-density sintered body. The sintering treatment is not particularly limited, and any conventionally known sintering treatment method can be suitably used. It is also possible to apply a heat treatment such as a gas carburizing heat treatment or a carbonitriding treatment after the sintering treatment.
以下、実施例に基づき本発明を具体的に説明する。
表１に、鉄基粉末として用いた各種粉末冶金用鉄粉（いずれも平均粒径：約80μm）の種類を示す。特に合金鋼粉の場合には、完全合金化鋼粉であるのか、部分合金化鋼粉であるのか、さらには完全合金化鋼粉に合金成分を部分拡散させたハイブリッド鋼粉であるのかの区別を示す。
Hereinafter, the present invention will be specifically described based on examples.
Table 1 shows the types of various iron powders for powder metallurgy used as iron-based powders (all of which have an average particle size of about 80 μm). Particularly in the case of alloy steel powder, it is distinguished whether it is a fully alloyed steel powder, a partially alloyed steel powder, or a hybrid steel powder in which the alloy components are partially diffused in the fully alloyed steel powder. Indicates.
表２に示す各種の鉄基粉末、天然黒鉛粉（平均粒径：５μm）および／または銅粉（平均粒径：25μm）に、各種添加材（１次添加材）を添加し、高速底部撹拌式混合機で混合しながら140℃に加熱した後、60℃以下に冷却し、さらに各種添加材（２次添加材）を添加し、500rpmで１分間撹拌後、混合機から混合粉末を排出した。１次および２次添加材の種類と添加量を 、表２に併記する。添加材の添加量（質量部）は、鉄基粉末と天然黒鉛粉と銅粉との合計質量：100mass％に対する比率を外数で示したものであるが、内数で表した数値とほぼ同じである。なお、タルク粉末、ステアタイト粉末の平均粒径はそれぞれ６μm、４μmであった。 Various additives (primary additive) are added to various iron-based powders, natural graphite powder (average particle size: 5 μm) and / or copper powder (average particle size: 25 μm) shown in Table 2, and high-speed bottom stirring is performed. After heating to 140 ° C. while mixing with a mixer, cool to 60 ° C. or below, add various additives (secondary additives), stir at 500 rpm for 1 minute, and then discharge the mixed powder from the mixer . Table 2 shows the types and amounts of primary and secondary additives. The additive amount (parts by mass) of the additive is the total mass of iron-based powder, natural graphite powder, and copper powder: the ratio to 100 mass% is indicated by an external number, but is almost the same as the numerical value expressed by the internal number It is. The average particle sizes of talc powder and steatite powder were 6 μm and 4 μm, respectively.
次に、得られた各鉄基粉末混合物を、室温下で、内径：11mmの超硬製タブレット型に充填し、686MPaで加圧成形した。その際、成形体を金型から抜出す時の抜出力および得られた成形体の圧粉密度を測定した。
さらに、得られた各鉄基粉末混合物を用いて、引張試験用の10×10×55mmの試験片と切削試験用の外径60mm×内径20mm×厚み30mmの試験片の圧粉成形を行った。圧粉成形の加圧力は784MPaとした。焼結はＲＸガス雰囲気中で行い、加熱温度を1130℃とし、加熱時間を20分とした。
引張試験用の10×10×55mm試験片から機械加工により平行部径：５mmの小型丸棒試験片を作製した。引張試験片については、一部は焼結の後、一部は浸炭熱処理を施した後、引張試験に供した。
焼結体の切削性については、サーメットの切削工具を用いて、切削速度：200m／分、送り：0.1mm／回、切込み深さ：0.3mm、切削距離：1000mの条件で切削試験を行い、切削工具の逃げ面の摩耗幅を測定した。切削工具の逃げ面の摩耗幅が小さいほど、焼結体の切削性が優れていることを示す。
得られた結果を表３に示す。
Next, each obtained iron-based powder mixture was filled into a cemented carbide tablet mold having an inner diameter of 11 mm at room temperature and pressure-molded at 686 MPa. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.
Furthermore, using each of the obtained iron-based powder mixtures, a 10 × 10 × 55 mm test piece for a tensile test and an outer diameter 60 mm × an inner diameter 20 mm × thickness 30 mm test piece for a cutting test were compacted. . The pressing force for compacting was 784 MPa. Sintering was performed in an RX gas atmosphere, the heating temperature was 1130 ° C., and the heating time was 20 minutes.
A small round bar test piece having a parallel part diameter of 5 mm was prepared by machining from a 10 × 10 × 55 mm test piece for a tensile test. The tensile test pieces were subjected to a tensile test, partly after sintering and partly subjected to carburizing heat treatment.
Regarding the machinability of the sintered body, a cutting test was performed using a cermet cutting tool under the conditions of cutting speed: 200 m / min, feed: 0.1 mm / turn, cutting depth: 0.3 mm, cutting distance: 1000 m, The wear width of the flank of the cutting tool was measured. It shows that the machinability of a sintered compact is excellent, so that the wear width of the flank of a cutting tool is small.
The obtained results are shown in Table 3.
表３に示した発明例と比較例との比較で明らかなように、潤滑剤として本発明の１次および２次添加材を添加することにより、高密度の成形体を極めて低い抜出力で成形することができ、また得られた焼結体および浸炭熱処理材の引張強度は高く、切削性も良好であった。 As is apparent from the comparison between the inventive examples shown in Table 3 and the comparative examples, by adding the primary and secondary additives of the present invention as a lubricant, a high-density molded body can be molded with a very low output power. Further, the obtained sintered body and the carburized heat treated material had high tensile strength and good machinability.
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