JP7432842B2 - Partial composite steel material and its manufacturing method - Google Patents
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- 229910000831 Steel Inorganic materials 0.000 title claims description 117
- 239000010959 steel Substances 0.000 title claims description 117
- 239000000463 material Substances 0.000 title claims description 114
- 239000002131 composite material Substances 0.000 title claims description 71
- 238000004519 manufacturing process Methods 0.000 title claims description 27
- 238000000034 method Methods 0.000 claims description 102
- 238000003756 stirring Methods 0.000 claims description 83
- 230000008569 process Effects 0.000 claims description 72
- 238000012545 processing Methods 0.000 claims description 26
- 238000010438 heat treatment Methods 0.000 claims description 21
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 20
- 238000011282 treatment Methods 0.000 claims description 19
- 239000000654 additive Substances 0.000 claims description 18
- 230000000996 additive effect Effects 0.000 claims description 17
- 230000009466 transformation Effects 0.000 claims description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 12
- 239000000126 substance Substances 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910045601 alloy Inorganic materials 0.000 claims description 5
- 239000000956 alloy Substances 0.000 claims description 5
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 claims description 2
- 229910039444 MoC Inorganic materials 0.000 claims description 2
- 239000012071 phase Substances 0.000 description 23
- 229910052799 carbon Inorganic materials 0.000 description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 12
- 239000002245 particle Substances 0.000 description 12
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 238000010586 diagram Methods 0.000 description 7
- 229910000734 martensite Inorganic materials 0.000 description 6
- 239000007769 metal material Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 150000004767 nitrides Chemical class 0.000 description 5
- 229910001562 pearlite Inorganic materials 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000005530 etching Methods 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- 229910000677 High-carbon steel Inorganic materials 0.000 description 3
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 229910010293 ceramic material Inorganic materials 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 229910017052 cobalt Inorganic materials 0.000 description 3
- 239000010941 cobalt Substances 0.000 description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 3
- 230000002301 combined effect Effects 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
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- 229910052751 metal Inorganic materials 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 238000002715 modification method Methods 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
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- 238000013461 design Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
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- 239000000523 sample Substances 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- GJNGXPDXRVXSEH-UHFFFAOYSA-N 4-chlorobenzonitrile Chemical compound ClC1=CC=C(C#N)C=C1 GJNGXPDXRVXSEH-UHFFFAOYSA-N 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- SJKRCWUQJZIWQB-UHFFFAOYSA-N azane;chromium Chemical compound N.[Cr] SJKRCWUQJZIWQB-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
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- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
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- 238000001816 cooling Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910052741 iridium Inorganic materials 0.000 description 1
- GKOZUEZYRPOHIO-UHFFFAOYSA-N iridium atom Chemical compound [Ir] GKOZUEZYRPOHIO-UHFFFAOYSA-N 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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- Other Surface Treatments For Metallic Materials (AREA)
Description
本発明は各種工業分野において使用される鉄鋼材の一部に硬質相を分散させることで、当該箇所の耐摩耗性を向上させた鉄鋼材及びその製造方法に関する。 The present invention relates to a steel material used in various industrial fields, in which a hard phase is dispersed in a part of the steel material to improve the wear resistance of the part, and a method for manufacturing the same.
近年、各種工業分野における製造工程や製品自体の高性能化及び自動生産システムの採用拡大に伴い、機械部品の性能の寿命に関わる耐摩耗性と、機械部品の形状を作りこむための加工性に優れた金属材が切望されている。 In recent years, with the improvement in the performance of manufacturing processes and products themselves in various industrial fields, and the increasing adoption of automated production systems, there has been an increase in wear resistance, which is related to the performance life of mechanical parts, and workability, which is required to create the shape of mechanical parts. Superior metal materials are in high demand.
一般的に、鉄鋼材の耐摩耗性を向上させるためには、セメンタイト相（Ｆｅ３Ｃ）よりも硬質な炭化物や窒化物などの硬質相の体積率を高めることが有効である。しかしながら、これらの硬質相を鉄鋼材の全体に分散させると、加工性、靭性及び疲労特性が低下することに加え、希少な金属元素を大量に添加するために経済性も損なう。 Generally, in order to improve the wear resistance of steel materials, it is effective to increase the volume fraction of hard phases such as carbides and nitrides that are harder than the cementite phase (Fe 3 C). However, when these hard phases are dispersed throughout the steel material, workability, toughness, and fatigue properties are reduced, and economic efficiency is also impaired due to the addition of large amounts of rare metal elements.
これに対して、特許文献１（特開２００５－２７２９１９号公報）では、摩擦攪拌接合法を応用して、アルミニウム合金からなるワークに分散質を分散させることによって当該箇所を複合化することで、局所的に耐摩耗性や潤滑性を向上させる技術が開示されている。 On the other hand, in Patent Document 1 (Japanese Unexamined Patent Publication No. 2005-272919), by applying the friction stir welding method and dispersing the dispersoid in a workpiece made of an aluminum alloy, the part concerned is composited. Techniques for locally improving wear resistance and lubricity have been disclosed.
前記特許文献１に記載の複合材料の製造方法においては、部材全体を諸特性の優れた材質で構成する必要がないので、コストが高騰することを回避することができ、ワークの肉を溶融することなく塑性流動させることができるので、摩擦攪拌後のワークにいわゆるブローホール等の欠陥が発生することがない。また、ワークの低融点成分が気化することがないので、ワークの組成が変化して該ワークが変質することもない。更に、ワークを溶融させることがないので、残留応力を小さくすることができるとともに、ワークの歪を小さくすることができるという利点があり、分散質の種類を適宜選択することによって、所望の特性を向上させることができる、とされている。 In the method for manufacturing a composite material described in Patent Document 1, the entire member does not need to be made of a material with excellent properties, so it is possible to avoid an increase in cost, and it is possible to avoid melting the flesh of the workpiece. Since plastic flow can be achieved without any friction stirring, defects such as so-called blowholes do not occur in the workpiece after friction stirring. Furthermore, since the low melting point components of the workpiece do not vaporize, the composition of the workpiece does not change and the quality of the workpiece does not change. Furthermore, since the workpiece is not melted, it has the advantage of reducing residual stress and distortion of the workpiece. By selecting the type of dispersoid appropriately, desired characteristics can be achieved. It is said that it can be improved.
また、特許文献２（特開２０１４－１７２０７２号公報）では、中・高炭素鋼の表面に対して摩擦攪拌処理を行う工程を含む中・高炭素鋼の表面改質方法が開示されている。また、当該表面改質方法においては、摩擦攪拌処理における中・高炭素鋼の表面温度を、Ａｃ１変態点を超えるようにすることや、Ａｃｍ変態点を超えるようにすることが開示されている。 Furthermore, Patent Document 2 (Japanese Unexamined Patent Publication No. 2014-172072) discloses a method for surface modification of medium/high carbon steel, which includes a step of performing a friction stir treatment on the surface of medium/high carbon steel. Furthermore, in the surface modification method, it is disclosed that the surface temperature of medium/high carbon steel in friction stir treatment is made to exceed the A c1 transformation point or to exceed the A cm transformation point. There is.
上記特許文献２に記載の表面改質方法においては、摩擦攪拌処理の工程において、炭素鋼の表面温度がＡｃｍ変態点を超えるように摩擦攪拌処理を行うことによって、水素脆化を特に抑制することができる、とされている。また、このような処理を行うことによって、炭素鋼の表面の組織を、パーライトとマルテンサイトとを含む組織とすることが可能である、とされている。 In the surface modification method described in Patent Document 2, hydrogen embrittlement is particularly suppressed by performing the friction stirring treatment so that the surface temperature of the carbon steel exceeds the A cm transformation point in the friction stirring treatment step. It is said that it is possible. Further, it is said that by performing such a treatment, it is possible to change the surface structure of carbon steel to a structure containing pearlite and martensite.
しかしながら、上記特許文献１に開示されている複合材料の製造方法及び特許文献２に開示されている表面改質方法では、摩擦攪拌処理を施した領域の硬度が著しく上昇し、当該領域を含む金属材の切断、切削加工及び塑性加工が困難となってしまう。その結果、任意の形状を有する金属部材を得ることが難しく、加工コストも大幅に増加してしまう。特に、被処理材が鉄鋼材の場合、摩擦攪拌処理に伴う相変態に起因して母材硬度が大幅に上昇し、これらの問題はより深刻となる。 However, in the composite material manufacturing method disclosed in Patent Document 1 and the surface modification method disclosed in Patent Document 2, the hardness of the area subjected to the friction stir treatment increases significantly, and the hardness of the area containing the area increases significantly. This makes cutting, machining, and plastic working of the material difficult. As a result, it is difficult to obtain a metal member having an arbitrary shape, and processing costs also increase significantly. In particular, when the material to be treated is a steel material, the hardness of the base material increases significantly due to phase transformation accompanying the friction stir treatment, making these problems more serious.
以上のような従来技術における問題点に鑑み、本発明の目的は、鉄鋼材の任意の領域を部分複合化する方法であって、簡便かつ効率的に所望の最終形状とした後に、部分複合化領域に高硬度及び優れた耐摩耗性を付与できる部分複合化鉄鋼材の製造方法を提供することにある。また、本発明は、良好な加工性を有する部分複合化鉄鋼材を提供することも目的としている。 In view of the above-mentioned problems in the prior art, an object of the present invention is to provide a method for partially composing an arbitrary region of a steel material. An object of the present invention is to provide a method for manufacturing a partially composite steel material that can impart high hardness and excellent wear resistance to a region. Another object of the present invention is to provide a partially composite steel material having good workability.
本発明者は上記目的を達成すべく、鉄鋼材の部分複合化方法について鋭意研究を重ねた結果、摩擦攪拌プロセスの処理温度を鉄鋼材の化学組成で決定されるＡ３点以下又はＡｃｍ点以下とすること等が極めて有効であることを見出し、本発明に到達した。 In order to achieve the above object, the present inventor has conducted intensive research on a method for partially composite steel materials, and as a result, the processing temperature of the friction stir process is determined by the chemical composition of the steel material at A 3 points or less or A cm point. We have found that the following is extremely effective, and have arrived at the present invention.
即ち、本発明は、
硬質相となる添加材を鉄鋼材の表面部位に供給し、前記表面部位に摩擦攪拌プロセスを施すことで前記鉄鋼材の任意の領域に前記添加材を分散させ、
前記摩擦攪拌プロセスの処理温度を前記鉄鋼材の化学組成で決定されるＡ３点以下又はＡｃｍ点以下とすること、
を特徴とする部分複合化鉄鋼材の製造方法、を提供する。
That is, the present invention
Supplying an additive that becomes a hard phase to a surface area of a steel material, applying a friction stirring process to the surface area to disperse the additive in any region of the steel material,
setting the processing temperature of the friction stir process to below A3 points or below A cm points determined by the chemical composition of the steel material;
Provided is a method for manufacturing a partially composite steel material characterized by the following.
ここで、摩擦攪拌プロセスの具体的な方法は、本発明の効果を損なわない限りにおいて特に限定されず、従来公知の種々の方法で摩擦攪拌プロセスを施すことができる。なお、摩擦攪拌プロセスとは、金属材の固相接合技術である摩擦攪拌接合（ＦＳＷ：Ｆｒｉｃｔｉｏｎ Ｓｔｉｒ Ｗｅｌｄｉｎｇ）を金属材の表面改質技術として利用するものである。 Here, the specific method of the friction stirring process is not particularly limited as long as it does not impair the effects of the present invention, and the friction stirring process can be performed by various conventionally known methods. Note that the friction stir process is a process that utilizes friction stir welding (FSW), which is a solid phase welding technology for metal materials, as a surface modification technology for metal materials.
また、鉄鋼材の表面部位への添加材の供給方法についても、本発明の効果を損なわない限りにおいて特に限定されず、従来公知の種々の方法を用いることができる。例えば、摩擦攪拌プロセス用ツールの進行方向前方に専用のノズル等を持いて供給してもよく、予め当該添加材を含むコーティングを施してもよく、摩擦攪拌プロセス用ツールから供給してもよい。ここで、添加材をより確実に鉄鋼材に分散させるためには、鉄鋼材の表面に溝を形成し、当該溝に添加材を充填することが好ましい。 Further, the method of supplying the additive to the surface portion of the steel material is not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known methods can be used. For example, a dedicated nozzle or the like may be provided in front of the friction stir process tool in the traveling direction, a coating containing the additive may be applied in advance, or the material may be supplied from the friction stir process tool. Here, in order to more reliably disperse the additive into the steel material, it is preferable to form grooves on the surface of the steel material and fill the grooves with the additive.
鉄鋼材の表面に形成させた溝に添加材を充填し、当該領域に摩擦攪拌プロセスを施す場合、予備工程として、底面に突起を有さない摩擦攪拌プロセス用ツールを用いて摩擦攪拌プロセスを施し、鉄鋼材表面のみに塑性流動を生じさせることで、蓋を形成することが好ましい。当該蓋によって、添加材の分散を目的として底面に突起を有する摩擦攪拌プロセス用ツールを用いて摩擦攪拌プロセスを施す際に、添加材の飛散を抑制することができる。 When filling grooves formed on the surface of a steel material with additives and performing a friction stir process on the area, as a preliminary step, the friction stir process is performed using a friction stir process tool that does not have protrusions on the bottom surface. It is preferable to form the lid by causing plastic flow only on the surface of the steel material. The lid can suppress scattering of the additive when performing a friction stir process using a friction stir process tool having protrusions on the bottom surface for the purpose of dispersing the additive.
また、本発明の部分複合化鉄鋼材の製造方法においては、摩擦攪拌プロセスの処理温度を鉄鋼材の化学組成で決定されるＡ３点以下又はＡｃｍ点以下とすることを特徴としている。Ａ３点以下又はＡｃｍ点以下の温度で摩擦攪拌プロセスを施すことで、オーステナイトに相変態しない領域が形成され、その後、硬質なパーライト、ベイナイト、マルテンサイト及びマッシブフェライト等が形成されない領域が形成されるため、複合化領域の加工性を確保することができる。即ち、部分的な硬化領域の形成を目的とする一般的な鉄鋼材の摩擦攪拌プロセスとは、完全に逆の発想である。 Furthermore, the method for producing a partially composite steel material of the present invention is characterized in that the treatment temperature of the friction stir process is set to below the A3 point or below the Acm point, which is determined by the chemical composition of the steel material. By performing the friction stirring process at a temperature of A 3 points or below or A cm points or below, a region where no phase transformation occurs in austenite is formed, and then a region where hard pearlite, bainite, martensite, massive ferrite, etc. are not formed is formed. Therefore, workability of the composite area can be ensured. That is, the concept is completely opposite to the general friction stirring process for steel materials, which aims to form partially hardened regions.
摩擦攪拌プロセスの処理温度の制御方法は、本発明の効果を損なわない限りにおいて特に限定されず、摩擦攪拌接合及び摩擦攪拌プロセスに関して従来公知の種々の方法を用いればよい。具体的には、摩擦攪拌プロセス用ツールの回転速度、移動速度及び印加荷重によって制御することができ、回転速度の低下、移動速度の増加及び印加荷重の低下によって処理温度を低下させることができる。その他、必要に応じて送風や水、液体窒素又は液体ＣＯ２等を用いた強制冷却を用いてもよい。 The method of controlling the processing temperature of the friction stir process is not particularly limited as long as it does not impair the effects of the present invention, and various methods conventionally known regarding friction stir welding and friction stir processes may be used. Specifically, it can be controlled by the rotation speed, movement speed, and applied load of the friction stir process tool, and the processing temperature can be lowered by decreasing the rotation speed, increasing the movement speed, and decreasing the applied load. In addition, forced cooling using air blowing, water, liquid nitrogen, liquid CO2 , etc. may be used as necessary.
本発明における摩擦攪拌プロセスとは、（１）摩擦攪拌プロセス用ツールを回転させつつ処理方向に向けて移動させる態様、（２）摩擦攪拌プロセス用ツールを回転させつつ処理位置で移動させない態様、（３）（１）で形成される処理領域を重畳させる態様、（４）（２）で形成される処理領域を重畳させる態様、及び（５）（１）～（４）の処理を任意に組み合わせる態様、が含まれる。 The friction stir process in the present invention includes (1) a mode in which the friction stir process tool is rotated and moved in the processing direction, (2) a mode in which the friction stir process tool is rotated but not moved at the processing position, ( 3) A mode in which the processing areas formed in (1) are overlapped, (4) a mode in which the processing areas formed in (2) are overlapped, and (5) the processes in (1) to (4) are arbitrarily combined. Aspects are included.
また、本発明の部分複合化鉄鋼材の製造方法においては、前記処理温度を前記鉄鋼材の化学組成で決定されるＡ１変態点以下とすること、が好ましい。処理温度を鉄鋼材の化学組成で決定されるＡ１変態点以下とすることで、オーステナイトへの相変態を完全に抑制することができ、硬質なパーライト、ベイナイト、マルテンサイト及びマッシブフェライト等の生成を完全に抑制することができる。その結果、複合化領域のより良好な加工性を確保することができる。 Further, in the method for producing a partially composite steel material of the present invention, it is preferable that the treatment temperature is set to a temperature equal to or lower than the A1 transformation point determined by the chemical composition of the steel material. By keeping the treatment temperature below the A1 transformation point determined by the chemical composition of the steel material, phase transformation to austenite can be completely suppressed and the formation of hard pearlite, bainite, martensite, massive ferrite, etc. can be completely suppressed. As a result, better workability of the composite region can be ensured.
また、本発明の部分複合化鉄鋼材の製造方法においては、前記摩擦攪拌プロセスを施した前記鉄鋼材を所望の機械部品の形状に加工する加工工程と、前記形状に加工した前記鉄鋼材に対して熱処理を施す熱処理工程と、を有すること、が好ましい。良好な加工性を有する部分複合化鉄鋼材を所望の機械部品の形状に加工した後に熱処理を施すことで、高硬度かつ優れた耐摩耗性を有する部分複合化領域が形成された鉄鋼製機械部品を、効率的かつ安価に得ることができる。なお、熱処理条件は、機械部品の必要特性を満足できる熱処理であればよく特に限定されないが、硬質相が基材に固溶しない温度範囲で熱処理することが好ましい。 The method for producing a partially composite steel material of the present invention further includes a processing step of processing the steel material subjected to the friction stir process into the shape of a desired mechanical part, and a step of processing the steel material processed into the shape into It is preferable to have a heat treatment step of performing heat treatment. A steel machine part in which a partially composite region with high hardness and excellent wear resistance is formed by processing a partially composite steel material with good workability into the desired shape of the machine part and then applying heat treatment. can be obtained efficiently and inexpensively. Note that the heat treatment conditions are not particularly limited as long as the heat treatment can satisfy the required characteristics of the mechanical component, but it is preferable to conduct the heat treatment in a temperature range in which the hard phase does not dissolve in the base material.
また、本発明の部分複合化鉄鋼材の製造方法においては、前記添加材にセラミックス材及び／又は、炭素又は窒素と結合することで炭化物又は窒化物を形成する金属材を含むこと、が好ましい。鉄鋼材にセラミックス材を分散させることで、当該領域の硬度及び耐摩耗性を向上させることができる。また、炭素又は窒素と結合することで炭化物又は窒化物を形成する金属材を分散させることで、摩擦攪拌プロセス中及び／又は熱処理によって、炭化物又は窒化物が形成し、複合化領域の硬度及び耐摩耗性を向上させることができる。硬質相の形態は特に限定されないが、粒状又は板状であることが好ましい。 Further, in the method for manufacturing a partially composite steel material of the present invention, it is preferable that the additive material includes a ceramic material and/or a metal material that forms a carbide or nitride by combining with carbon or nitrogen. By dispersing the ceramic material in the steel material, the hardness and wear resistance of the region can be improved. Additionally, by dispersing metal materials that form carbides or nitrides when combined with carbon or nitrogen, carbides or nitrides are formed during the friction stir process and/or by heat treatment, increasing the hardness and resistance of the composite region. Abrasion resistance can be improved. Although the form of the hard phase is not particularly limited, it is preferably granular or plate-like.
セラミックス材としては、鉄鋼材料の相変態により形成されるマルテンサイト相やセメンタイト相よりも硬質な炭化タングステン、炭化モリブデン、窒化チタン及び窒化クロム等を好適に使用することができるが、炭化タングステンを用いることがより好ましい。炭化タングステンを鉄鋼材に分散させることにより、高い硬度を有する炭化タングステンの複合効果に加え、炭化タングステンから分解した炭素が鉄鋼材に供給され、熱処理を施すことによって、当該炭素に起因する析出物の形成や変態相の高硬度化が期待できる。また、炭素や窒素と結合し、硬質な炭化物又は窒化物を形成する金属材としては、タングステン、モリブデン、チタン、ニオブ、ジルコニウム、クロム及びコバルト等を用いることができる。 As the ceramic material, tungsten carbide, molybdenum carbide, titanium nitride, chromium nitride, etc., which are harder than the martensitic phase or cementite phase formed by phase transformation of steel materials, can be preferably used, but tungsten carbide is used. It is more preferable. By dispersing tungsten carbide into steel materials, in addition to the combined effect of tungsten carbide with high hardness, carbon decomposed from tungsten carbide is supplied to the steel materials, and by heat treatment, precipitates caused by the carbon are eliminated. Higher hardness of the formed and transformed phases can be expected. Further, as the metal material that combines with carbon and nitrogen to form a hard carbide or nitride, tungsten, molybdenum, titanium, niobium, zirconium, chromium, cobalt, etc. can be used.
更に、本発明の部分複合化鉄鋼材の製造方法においては、前記鉄鋼材が純鉄、普通鋼、特殊鋼及び鉄基合金のうちのいずれかであること、が好ましい。鉄鋼材の種類については、本発明の効果を損なわない限りにおいて特に限定されず、従来公知の種々の鉄鋼材を用いることができるが、純鉄、普通鋼、特殊鋼及び鉄基合金のうちのいずれかとすることで、部分複合化鉄鋼材を機械部品として好適に使用することができる。 Furthermore, in the method for producing a partially composite steel material of the present invention, it is preferable that the steel material is any one of pure iron, common steel, special steel, and iron-based alloy. The type of steel material is not particularly limited as long as it does not impair the effects of the present invention, and various conventionally known steel materials can be used, including pure iron, ordinary steel, special steel, and iron-based alloys. In either case, the partially composite steel material can be suitably used as a mechanical component.
また、本発明は、
鉄鋼材の任意の領域に硬質粒子が分散した部分複合化領域が形成され、
前記鉄鋼材の炭素含有量が０．２～１．２質量％であり、
前記部分複合化領域のビッカース硬度が前記鉄鋼材のビッカース硬度の３倍以下であること、
を特徴とする部分複合化鉄鋼材、も提供する。
Moreover, the present invention
A partially composite region in which hard particles are dispersed is formed in any region of the steel material,
The carbon content of the steel material is 0.2 to 1.2% by mass,
The Vickers hardness of the partially composited region is not more than three times the Vickers hardness of the steel material;
We also provide partially composite steel materials featuring:
本発明の部分複合化鉄鋼材は、高い硬度と優れた耐摩耗性を有する部分複合化領域が形成された鉄鋼製機械部品を製造するために好適に用いることができ、炭素含有量が０．２～１．２質量％であるにもかかわらず、部分複合化領域のビッカース硬度が鉄鋼材の３倍以下に抑えられている（部分複合化領域の硬度上昇が小さい）。その結果、良好な加工性を有する部分複合化鉄鋼材を所望の機械部品の形状に加工した後に熱処理を施すことで、高硬度かつ優れた耐摩耗性を有する部分複合化領域が形成された鉄鋼製機械部品を、効率的かつ安価に得ることができる。なお、鉄鋼材の炭素含有量は０．２～１．２質量％であることから、十分な強度を有している。 The partially composite steel material of the present invention can be suitably used to manufacture a steel machine part in which a partially composite region having high hardness and excellent wear resistance is formed, and has a carbon content of 0. Even though the content is 2 to 1.2% by mass, the Vickers hardness in the partially composited region is suppressed to three times or less that of the steel material (hardness increase in the partially composited region is small). As a result, by processing the partially composite steel material with good workability into the shape of the desired mechanical part and then applying heat treatment, the steel material has a partially composite region with high hardness and excellent wear resistance. Machine parts can be obtained efficiently and at low cost. Note that since the carbon content of the steel material is 0.2 to 1.2% by mass, it has sufficient strength.
また、本発明の部分複合化鉄鋼材においては、前記硬質粒子が炭化タングステンであること、が好ましい。炭化タングステンの分散により、高い硬度を有する炭化タングステンの複合効果が得られることに加え、炭化タングステンから分解した炭素が鉄鋼材に供給され、熱処理によって形成される析出物や高硬度な変態相によって、部分複合化領域に極めて高い硬度と耐摩耗性が付与される。 Moreover, in the partially composite steel material of the present invention, it is preferable that the hard particles are tungsten carbide. By dispersing tungsten carbide, in addition to obtaining the combined effect of tungsten carbide with high hardness, the carbon decomposed from tungsten carbide is supplied to the steel material, and the precipitates and high hardness transformation phases formed by heat treatment, Extremely high hardness and wear resistance are imparted to the partially composite area.
更に、本発明の部分複合化鉄鋼材においては、前記部分複合化領域における前記硬質粒子の割合が０．５～８体積％であること、が好ましい。硬質粒子の割合が０．５体積％以上であることで、部分複合化領域に高い硬度及び耐摩耗性を付与することができ、８体積％以下とすることで、硬質粒子の凝集領域等に起因する脆化を抑制することができる。 Further, in the partially composited steel material of the present invention, it is preferable that the proportion of the hard particles in the partially composited region is 0.5 to 8% by volume. By setting the proportion of hard particles to 0.5% by volume or more, high hardness and wear resistance can be imparted to the partially composite region, and by setting the proportion to 8% by volume or less, it is possible to impart high hardness and wear resistance to the agglomerated region of hard particles. The resulting embrittlement can be suppressed.
なお、本発明の部分複合化鉄鋼材は、本発明の部分複合化鉄鋼材の製造方法によって好適に製造することができる。 The partially composite steel material of the present invention can be suitably manufactured by the method for producing a partially composite steel material of the present invention.
本発明によれば、鉄鋼材の任意の領域を部分複合化する方法であって、簡便かつ効率的に所望の最終形状とした後に、部分複合化領域に高硬度及び優れた耐摩耗性を付与できる部分複合化鉄鋼材の製造方法を提供することができる。また、本発明によれば、良好な加工性を有する部分複合化鉄鋼材を提供することができる。 According to the present invention, there is provided a method for partially compounding an arbitrary region of a steel material, and after forming the desired final shape simply and efficiently, imparting high hardness and excellent wear resistance to the partially composited region. It is possible to provide a method for manufacturing a partially composite steel material that can be produced. Further, according to the present invention, a partially composite steel material having good workability can be provided.
以下、図面を参照しながら本発明の部分複合化鉄鋼材及びその製造方法について詳細に説明するが、本発明はこれらのみに限定されるものではない。なお、以下の説明では、同一または相当部分には同一符号を付し、重複する説明は省略する場合がある。また、図面は、本発明を概念的に説明するためのものであるから、表された各構成要素の寸法やそれらの比は実際のものとは異なる場合もある。 Hereinafter, the partially composite steel material of the present invention and its manufacturing method will be described in detail with reference to the drawings, but the present invention is not limited thereto. In the following description, the same or equivalent parts are given the same reference numerals, and redundant descriptions may be omitted. Further, since the drawings are for conceptually explaining the present invention, the dimensions of the illustrated components and their ratios may differ from the actual ones.
（１）部分複合化鉄鋼材の製造方法
ここでは、本発明の部分複合化鉄鋼材の製造方法の一態様として、鉄鋼材の表面に形成した溝に添加材を充填し、当該領域に対して摩擦攪拌プロセスを施す方法について詳細に説明する。
(1) Method for manufacturing partially composite steel materials Here, as one aspect of the method for manufacturing partially composite steel materials of the present invention, grooves formed on the surface of the steel material are filled with an additive material, and the area is The method of applying the friction stir process will be explained in detail.
図１及び図２は、本発明の部分複合化鉄鋼材の製造方法の模式図である。図１は予備処理、図２は部分複合化領域を形成させる摩擦攪拌プロセスを示している。鉄鋼材２の耐摩耗性が必要とされる領域４内に凹部６を設け、凹部６に添加材８を充填する。次に、添加材８を充填させた凹部６の幅よりも大きな予備処理摩擦攪拌プロセス用ツール１０を回転させつつ下降させ、凹部６を含む鉄鋼材２の表面に押し当てる。これにより、凹部６の周辺の鉄鋼材２が摩擦攪拌によって塑性流動し、当該塑性流動によって凹部６の表面に鉄鋼材２からなる蓋１２が形成される。ここで、予備処理摩擦攪拌プロセス用ツール１０の底面には突起（プローブ）を設けていない。 FIGS. 1 and 2 are schematic diagrams of the method for manufacturing a partially composite steel material of the present invention. FIG. 1 shows a preliminary treatment, and FIG. 2 shows a friction stir process for forming a partially composite region. A recess 6 is provided in a region 4 of the steel material 2 where wear resistance is required, and the recess 6 is filled with an additive 8. Next, the pretreatment friction stir process tool 10, which is larger in width than the recess 6 filled with the additive 8, is rotated and lowered, and pressed against the surface of the steel material 2 including the recess 6. As a result, the steel material 2 around the recess 6 plastically flows due to friction stirring, and the lid 12 made of the steel material 2 is formed on the surface of the recess 6 due to the plastic flow. Here, no protrusion (probe) is provided on the bottom surface of the pretreatment friction stir process tool 10.
予備処理における摩擦攪拌プロセスの条件は特に限定されないが、鉄鋼材２の化学組成で決定されるＡ３点以上又はＡｃｍ点以上とすることで、鉄鋼材２の塑性流動が円滑になり、蓋１２を容易に形成することができる。また、処理温度を高くすると予備処理摩擦攪拌プロセス用ツール１０の温度は上昇するものの、印加されるプロセス荷重を低減することができる。 The conditions of the friction stir process in the preliminary treatment are not particularly limited, but by setting the A point or more or the A cm point or more, which is determined by the chemical composition of the steel material 2, the plastic flow of the steel material 2 becomes smooth, and the lid 12 can be easily formed. Furthermore, although increasing the processing temperature increases the temperature of the pretreatment friction stir process tool 10, the applied process load can be reduced.
次に、底面に突起を有する摩擦攪拌プロセス用ツール１４を用いて、蓋１２が形成された凹部６に対して摩擦攪拌プロセスを施すことで、硬質相が分散した部分複合化領域が形成される。摩擦攪拌プロセス用ツール１４のプローブの長さは、所望の部分複合化領域の厚さに応じて決定すればよい。 Next, a friction stir process is performed on the recess 6 in which the lid 12 is formed using a friction stir process tool 14 having a protrusion on the bottom surface, thereby forming a partially composite region in which the hard phase is dispersed. . The length of the probe of the friction stir process tool 14 may be determined depending on the desired thickness of the partially composited region.
部分複合化領域を形成させる場合の摩擦攪拌プロセスの処理温度は鉄鋼材２の化学組成で決定されるＡ３点以下又はＡｃｍ点以下であり、Ａ１点以下とすることがより好ましい。Ａ３点以下又はＡｃｍ点以下の温度で摩擦攪拌プロセスを施すことで、オーステナイトに相変態しない領域が形成され、硬質なパーライト、ベイナイト、マルテンサイト及びマッシブフェライト等が形成されない領域が形成されるため、複合化領域の加工性を確保することができる。また、処理温度を鉄鋼材２の化学組成で決定されるＡ１変態点以下とすることで、オーステナイトへの相変態を完全に抑制することができ、硬質なパーライト、ベイナイト、マルテンサイト及びマッシブフェライト等の生成を完全に抑制することができる。その結果、複合化領域のより良好な加工性を確保することができる。 The processing temperature of the friction stir process when forming a partially composite region is determined by the chemical composition of the steel material 2 at an A point of 3 or less or an A cm point or less, and more preferably an A of 1 point or less. By performing the friction stirring process at a temperature of A 3 points or below or A cm points or below, a region where austenite does not undergo phase transformation is formed, and a region where hard pearlite, bainite, martensite, massive ferrite, etc. is not formed is formed. Therefore, workability of the composite area can be ensured. In addition, by setting the treatment temperature to below the A1 transformation point determined by the chemical composition of the steel material 2, phase transformation to austenite can be completely suppressed, resulting in hard pearlite, bainite, martensite, and massive ferrite. etc. can be completely suppressed. As a result, better workability of the composite region can be ensured.
ここで、摩擦攪拌プロセス用ツール１４の回転速度、移動速度及び印加荷重によって処理温度を制御することができ、特に、回転速度によって効果的に処理温度を制御することができる。摩擦攪拌プロセス用ツール１４の材質、形状及びサイズや鉄鋼材２の組成及び組織、凹部６のサイズ及び添加材８の種類等にも依存するが、例えば、超硬合金製でショルダ径が１０～１５ｍｍ程度の摩擦攪拌プロセス用ツール１４を用いて炭素鋼に処理を施す場合、回転速度を１５０ｒｐｍ以下、好ましくは１００ｒｐｍ以下、より好ましくは８０ｒｐｍ以下とすることで、処理温度をＡ１点以下とすることができる。 Here, the processing temperature can be controlled by the rotation speed, movement speed, and applied load of the friction stir process tool 14, and in particular, the processing temperature can be effectively controlled by the rotation speed. Although it depends on the material, shape and size of the friction stir process tool 14, the composition and structure of the steel material 2, the size of the recess 6 and the type of additive 8, for example, it is made of cemented carbide and has a shoulder diameter of 10~ When treating carbon steel using a friction stir process tool 14 of about 15 mm, the rotation speed is set to 150 rpm or less, preferably 100 rpm or less, more preferably 80 rpm or less, so that the treatment temperature is A1 point or less. be able to.
摩擦攪拌プロセス用ツール１４を用いた摩擦攪拌プロセスは複数回行ってもよく、複数回の処理によって硬質相をより均一に分散させることができる。ここで、摩擦攪拌プロセスで形成される攪拌部（部分複合化領域）の組織及び硬質相の分散状況は処理方向に対して左右非対称となる。これに対し、摩擦攪拌プロセス用ツール１４の回転方向を逆にして摩擦攪拌プロセスを重畳させるか、摩擦攪拌プロセスの開始位置と終了位置を逆にして摩擦攪拌プロセスを重畳させることにより、当該非対称性を改善することができる。 The friction stirring process using the friction stirring process tool 14 may be performed multiple times, and the hard phase can be more uniformly dispersed by multiple treatments. Here, the structure of the stirred part (partial composite region) formed by the friction stirring process and the state of dispersion of the hard phase are asymmetrical with respect to the processing direction. On the other hand, by reversing the rotational direction of the friction stirring process tool 14 and overlapping the friction stirring process, or by reversing the starting and ending positions of the friction stirring process and overlapping the friction stirring process, the asymmetry can be prevented. can be improved.
予備処理摩擦攪拌プロセス用ツール１０及び摩擦攪拌プロセス用ツール１４の材質は、例えば、タングステンカーバイト（ＷＣ）、コバルト（Ｃｏ）、ニッケル（Ｎｉ）からなる超硬合金、コバルト（Ｃｏ）基合金、イリジウム（Ｉｒ）、タングステン（Ｗ）等の高融点金属及びその合金、またはＳｉ３Ｎ４及びＰＣＢＮ等のセラミックスからなるものとすることができる。 The materials of the pretreatment friction stir process tool 10 and the friction stir process tool 14 include, for example, a cemented carbide made of tungsten carbide (WC), cobalt (Co), and nickel (Ni), a cobalt (Co)-based alloy, It can be made of high melting point metals such as iridium (Ir) and tungsten (W) and their alloys, or ceramics such as Si 3 N 4 and PCBN.
摩擦攪拌プロセス用ツール１４を用いた摩擦攪拌プロセスを施した鉄鋼材２を所望の機械部品の形状に加工した後、部分複合化領域を含む領域に対して熱処理を施すことで、高硬度かつ優れた耐摩耗性を有する部分複合化領域が形成された鉄鋼製機械部品を、効率的かつ安価に得ることができる。なお、熱処理条件は、機械部品の必要特性を満足できる熱処理であればよく特に限定されないが、硬質相が鉄鋼材２に固溶しない温度範囲で熱処理することが好ましい。 After processing the steel material 2 that has been subjected to the friction stir process using the friction stir process tool 14 into the shape of the desired mechanical part, heat treatment is applied to the region including the partially composite region, resulting in high hardness and excellent It is possible to efficiently and inexpensively obtain a steel machine component in which a partially composite region having wear resistance is formed. Note that the heat treatment conditions are not particularly limited as long as the heat treatment can satisfy the required characteristics of the mechanical component, but it is preferable to conduct the heat treatment in a temperature range in which the hard phase does not dissolve in the steel material 2.
熱処理の方法は、本発明の効果を損なわない限りにおいて特に限定されず、従来公知の種々の熱処理方法を用いることができるが、レーザ焼入れ、高周波誘導加熱焼入れ及び火炎焼入れ等の局所的な焼入れ処理を用いて部分複合化領域に対して熱処理を施すことで、最小限のエネルギー消費で高硬度領域を得ることができる。 The heat treatment method is not particularly limited as long as it does not impair the effects of the present invention, and various conventionally known heat treatment methods can be used, including local hardening treatments such as laser hardening, high-frequency induction heating hardening, and flame hardening. By applying heat treatment to the partially composited region using the method, a high hardness region can be obtained with minimal energy consumption.
（２）部分複合化鉄鋼材
図３は、本発明の部分複合化鉄鋼材の模式図である。部分複合化鉄鋼材２０は、鉄鋼材２を基材とし、部分複合化領域２２を有している。また、図４に、部分複合化鉄鋼材２０から鉄鋼製機械部品３０を製造する模式図を示す。なお、鉄鋼製機械部品３０は部分複合化領域２２を刃先とする工業用刃物である。
(2) Partially Composite Steel Material FIG. 3 is a schematic diagram of the partially composite steel material of the present invention. The partially composited steel material 20 uses the steel material 2 as a base material and has a partially composited region 22 . Further, FIG. 4 shows a schematic diagram of manufacturing a steel machine part 30 from the partially composite steel material 20. Note that the steel machine component 30 is an industrial cutter having the partially composite region 22 as a cutting edge.
鉄鋼材２の炭素含有量は０．２～１．２質量％であり、硬質粒子が分散しているにもかかわらず、部分複合化領域２２のビッカース硬度は鉄鋼材２の３倍以下に抑えられている。その結果、良好な加工性を有する部分複合化鉄鋼材２０を鉄鋼製機械部品３０の形状に加工した後に熱処理を施すことで、高硬度かつ優れた耐摩耗性を有する部分複合化領域２２を刃先とする鉄鋼製機械部品３０を、効率的かつ安価に得ることができる。なお、鉄鋼材２の炭素含有量は０．２～１．２質量％であることから、工業用刃物の基材として十分な強度を有している。 Although the carbon content of the steel material 2 is 0.2 to 1.2% by mass and the hard particles are dispersed, the Vickers hardness of the partially composite region 22 is suppressed to less than three times that of the steel material 2. It is being As a result, by heat-treating the partially composite steel material 20 with good workability into the shape of the steel machine part 30, the partially composite region 22 with high hardness and excellent wear resistance is formed at the cutting edge. A steel machine component 30 having the following properties can be obtained efficiently and at low cost. Note that since the carbon content of the steel material 2 is 0.2 to 1.2% by mass, it has sufficient strength as a base material for industrial cutlery.
部分複合化領域２２に分散する硬質粒子は炭化タングステンであることが好ましい。炭化タングステンの分散により、高い硬度を有する炭化タングステンの複合効果が得られることに加え、炭化タングステンから分解した炭素が鉄鋼材２に供給され、熱処理によって形成される析出物や高硬度な変態相によって、部分複合化領域２２に極めて高い硬度と耐摩耗性が付与される。 The hard particles dispersed in the partially composited region 22 are preferably tungsten carbide. By dispersing tungsten carbide, in addition to obtaining the combined effect of tungsten carbide with high hardness, carbon decomposed from tungsten carbide is supplied to the steel material 2, and the precipitates formed by heat treatment and the highly hard transformed phase , extremely high hardness and wear resistance are imparted to the partially composite region 22.
また、部分複合化領域２２における硬質粒子の割合は０．５～８体積％であることが好ましい。硬質粒子の割合が０．５体積％以上であることで、部分複合化領域２２に高い硬度及び耐摩耗性を付与することができ、８体積％以下とすることで、硬質粒子の凝集領域等に起因する脆化を抑制することができる。 Further, the proportion of hard particles in the partially composite region 22 is preferably 0.5 to 8% by volume. When the ratio of hard particles is 0.5% by volume or more, high hardness and wear resistance can be imparted to the partially composite region 22, and when the ratio is 8% by volume or less, hard particle agglomeration regions, etc. embrittlement caused by this can be suppressed.
以上、本発明の代表的な実施形態について説明したが、本発明はこれらのみに限定されるものではなく、種々の設計変更が可能であり、それら設計変更は全て本発明の技術的範囲に含まれる。 Although typical embodiments of the present invention have been described above, the present invention is not limited to these, and various design changes are possible, and all such design changes are included within the technical scope of the present invention. It will be done.
≪実施例≫
２００ｍｍ×１００ｍｍ×２ｍｍの鋼板（Ｆｅ－０．８質量％Ｃ）の中央に幅０．５ｍｍ×長さ２００ｍｍ×深さ１ｍｍの溝状の凹部を設け、当該凹部に平均粒径１．０μｍの炭化タングステン粉末を充填した。
≪Example≫
A groove-shaped recess with a width of 0.5 mm, a length of 200 mm, and a depth of 1 mm was provided in the center of a 200 mm x 100 mm x 2 mm steel plate (Fe-0.8 mass % C), and a groove-like recess with an average grain size of 1.0 μm was provided in the recess. Filled with tungsten carbide powder.
次に、図１に示す態様で、直径１２ｍｍの円柱状の超硬合金製予備処理摩擦攪拌プロセス用ツール（底面の突起なし）を用い、炭化タングステン粉末を充填した凹部に予備摩擦攪拌プロセスを施し、凹部の表面に蓋を形成させた。摩擦攪拌プロセス条件は、ツール回転速度を２７５ｒｐｍ、移動速度を２５０ｍｍ／ｍｉｎ、印加荷重を２１００ｋｇとした。 Next, in the manner shown in Fig. 1, a pretreatment friction stir process tool made of cylindrical cemented carbide with a diameter of 12 mm (without protrusions on the bottom) was used to perform a preliminary friction stir process on the recess filled with tungsten carbide powder. , a lid was formed on the surface of the recess. The friction stir process conditions were a tool rotation speed of 275 rpm, a moving speed of 250 mm/min, and an applied load of 2100 kg.
次に、図２に示す態様で、直径１２ｍｍの円柱状の超硬合金製摩擦攪拌プロセス用ツール（底面に長さ１．８ｍｍ、直径４ｍｍの突起を有する）を用い、蓋を形成させた凹部に摩擦攪拌プロセスを施した。摩擦攪拌プロセス条件は、ツール回転速度を１００ｒｐｍ、移動速度を１００ｍｍ／ｍｉｎ、印加荷重を３５００ｋｇとした。 Next, in the manner shown in Fig. 2, a cylindrical cemented carbide friction stir process tool with a diameter of 12 mm (having a protrusion of 1.8 mm in length and 4 mm in diameter on the bottom) was used to form a recess with a lid. was subjected to a friction stir process. The friction stir process conditions were a tool rotation speed of 100 rpm, a moving speed of 100 mm/min, and an applied load of 3500 kg.
摩擦攪拌プロセスを施した部分複合化領域表面の外観写真を図５に示す。クラック等は認められず、良好な表面状態となっている。部分複合化領域の断面写真を図６に、２％ナイタルでエッチングを施した部分複合化領域の断面写真を図７に、それぞれ示す。図６の断面写真から、炭化タングステン粉末が僅かに凝集している領域は存在するが、処理部に欠陥等は認められず、良好な部分複合化領域が形成されていることが確認できる。また、図７の断面写真から、良好な攪拌領域（攪拌部）が形成されていることが確認できる。なお、摩擦攪拌プロセスのツール回転速度を１００ｒｐｍと極めて小さな値に設定したことで、摩擦攪拌プロセスの処理温度が鋼板（Ｆｅ－０．８質量％Ｃ）のＡｃｍ未満になったと考えられる。 Figure 5 shows an external photograph of the surface of the partially composited region subjected to the friction stir process. No cracks were observed and the surface was in good condition. A cross-sectional photograph of the partially composite region is shown in FIG. 6, and a cross-sectional photograph of the partially composite region etched with 2% nital is shown in FIG. From the cross-sectional photograph in FIG. 6, it can be seen that although there is a region where the tungsten carbide powder is slightly aggregated, no defects are observed in the treated area, and a good partially composite region is formed. Further, from the cross-sectional photograph in FIG. 7, it can be confirmed that a good stirring region (stirring portion) was formed. It is believed that by setting the tool rotation speed in the friction stir process to an extremely small value of 100 rpm, the treatment temperature in the friction stir process became less than A cm of the steel plate (Fe-0.8 mass % C).
部分複合化領域断面のビッカース硬度の水平分布を図８に示す。部分複合化領域の硬度は炭化タングステン粒子の分散等によって上昇しているが、母材のビッカース硬度２００ＨＶに対して６００ＨＶ未満となっており、部分複合化領域のビッカース硬度は母材の３倍以下となっている。なお、硬度測定は荷重：０．１ｋｇｆ、荷重負荷時間：１５ｓとした。測定位置は最表面から深さ０．５ｍｍとし、当該深さにおける水平方向の硬度プロファイルを測定した。 FIG. 8 shows the horizontal distribution of Vickers hardness in the cross section of the partially composite region. Although the hardness of the partially composite region has increased due to the dispersion of tungsten carbide particles, it is less than 600 HV compared to the Vickers hardness of the base material of 200 HV, and the Vickers hardness of the partially composite region is less than three times that of the base material. It becomes. The hardness was measured under a load of 0.1 kgf and a loading time of 15 seconds. The measurement position was 0.5 mm deep from the outermost surface, and the horizontal hardness profile at this depth was measured.
≪比較例≫
超硬合金製摩擦攪拌プロセス用ツールを用いた摩擦攪拌プロセスの条件を、ツール回転速度を３００ｒｐｍ、移動速度を１００ｍｍ／ｍｉｎ、印加荷重を２０００ｋｇとしたこと以外は実施例と同様にして、部分複合化領域を形成させた。
≪Comparative example≫
The conditions for the friction stir process using a cemented carbide friction stir process tool were the same as in the example except that the tool rotation speed was 300 rpm, the moving speed was 100 mm/min, and the applied load was 2000 kg. The area formed was
部分複合化領域表面の外観写真を図９に示す。また、部分複合化領域の断面写真を図１０に、２％ナイタルでエッチングを施した部分複合化領域の断面写真を図１１に、それぞれ示す。部分複合化領域の中心に、摩擦攪拌プロセスの処理温度が高温になったことに起因する大きな割れが生じている。ツール回転速度を３００ｒｐｍとしたことで、摩擦攪拌プロセスの処理温度が鋼板（Ｆｅ－０．８質量％Ｃ）のＡ３点を超えたものと考えらえる。 FIG. 9 shows an external photograph of the surface of the partially composited region. Further, a cross-sectional photograph of the partially composite region is shown in FIG. 10, and a cross-sectional photograph of the partially composite region etched with 2% nital is shown in FIG. 11, respectively. A large crack occurs in the center of the partially composited region due to the high temperature of the friction stir process. It is thought that by setting the tool rotation speed to 300 rpm, the processing temperature of the friction stir process exceeded the A3 point of the steel plate (Fe-0.8 mass % C).
部分複合化領域断面のビッカース硬度の水平分布を図８に示す。部分複合化領域の硬度は炭化タングステン粒子の分散及び母材の相変態に起因して大幅に上昇し、母材のビッカース硬度２００ＨＶに対して８００ＨＶ以上となっている。 FIG. 8 shows the horizontal distribution of Vickers hardness in the cross section of the partially composite region. The hardness of the partially composite region increases significantly due to the dispersion of tungsten carbide particles and the phase transformation of the base material, and is now 800 HV or more compared to the Vickers hardness of the base material of 200 HV.
２・・・鉄鋼材、
４・・・耐摩耗性が必要とされる領域、
６・・・凹部、
８・・・添加材、
１０・・・予備処理摩擦攪拌プロセス用ツール、
１２・・・蓋、
１４・・・摩擦攪拌プロセス用ツール、
２０・・・部分複合化鉄鋼材、
２２・・・部分複合化領域、
３０・・・鉄鋼製機械部品。
2...Steel materials,
4... Area where wear resistance is required,
6... recess,
8...Additive material,
10...Pretreatment friction stir process tool,
12... Lid,
14...Tool for friction stir process,
20...partially composite steel material,
22... Partial composite area,
30... Steel machine parts.
Claims (3)
前記摩擦攪拌プロセスの処理温度を前記鉄鋼材の化学組成で決定されるＡ３点以下又はＡｃｍ点以下とし、
前記摩擦攪拌プロセスを施した前記鉄鋼材を所望の機械部品の形状に加工する加工工程と、
前記形状に加工した前記鉄鋼材に対して熱処理を施す熱処理工程と、を有し、
前記加工工程において、前記摩擦攪拌プロセスによって形成された複合化領域を加工し、
前記添加材を炭化タングステン又は炭化モリブデンとすること、
を特徴とする鉄鋼製機械部品の製造方法。 Supplying an additive that becomes a hard phase to a surface area of a steel material, applying a friction stirring process to the surface area to disperse the additive in any region of the steel material,
The processing temperature of the friction stir process is set to below A 3 points or below A cm points determined by the chemical composition of the steel material,
a processing step of processing the steel material subjected to the friction stir process into the shape of a desired mechanical part;
a heat treatment step of performing heat treatment on the steel material processed into the shape,
In the processing step, processing the composite region formed by the friction stir process ,
The additive material is tungsten carbide or molybdenum carbide;
A method for manufacturing steel machine parts, characterized by:
を特徴とする請求項１に記載の鉄鋼製機械部品の製造方法。 setting the treatment temperature to be below the A1 transformation point determined by the chemical composition of the steel material;
The method for manufacturing a steel machine component according to claim 1, characterized in that:
を特徴とする請求項１又は２に記載の鉄鋼製機械部品の製造方法。 The steel material is any one of pure iron, ordinary steel, special steel, and iron-based alloy;
The method for manufacturing a steel machine component according to claim 1 or 2 , characterized in that:
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| WO2009041665A1 (en) | 2007-09-27 | 2009-04-02 | Osaka City | Method for refining texture of ferrous material, and ferrous material and blade having microscopic texture |
| WO2011118784A1 (en) | 2010-03-25 | 2011-09-29 | 地方独立行政法人大阪市立工業研究所 | Method for forming metal membrane |
| JP2017094474A (en) | 2015-11-27 | 2017-06-01 | 株式会社Ａｍｃ | Cutter made of cemented carbide and manufacturing method thereof |
| JP2018153848A (en) | 2017-03-17 | 2018-10-04 | 国立大学法人大阪大学 | Weld part modification method |
| JP2019195858A (en) | 2018-05-08 | 2019-11-14 | 株式会社Ａｍｃ | Cemented carbide round blade and its manufacturing method |
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| JP2007530791A (en) | 2004-03-24 | 2007-11-01 | エスアイアイ・メガダイアモンド・インコーポレーテッド | Solid state processing of materials by friction stir processing and friction stir mixing |
| WO2009041665A1 (en) | 2007-09-27 | 2009-04-02 | Osaka City | Method for refining texture of ferrous material, and ferrous material and blade having microscopic texture |
| WO2011118784A1 (en) | 2010-03-25 | 2011-09-29 | 地方独立行政法人大阪市立工業研究所 | Method for forming metal membrane |
| JP2017094474A (en) | 2015-11-27 | 2017-06-01 | 株式会社Ａｍｃ | Cutter made of cemented carbide and manufacturing method thereof |
| JP2018153848A (en) | 2017-03-17 | 2018-10-04 | 国立大学法人大阪大学 | Weld part modification method |
| JP2019195858A (en) | 2018-05-08 | 2019-11-14 | 株式会社Ａｍｃ | Cemented carbide round blade and its manufacturing method |
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