JP2021063297A - Iron-copper alloy having high thermal conductivity and method for producing the same - Google Patents
Iron-copper alloy having high thermal conductivity and method for producing the same Download PDFInfo
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Abstract
Description
本発明は鉄(Fe)をベースとして適量の銅(Cu)を含む新規な鉄−銅(Fe−Cu)合金に関し、より詳しくは、高い熱伝導性を有しながら、優れた機械的な物性、電磁気波遮蔽性及び軟磁性などを有する鉄−銅合金及びその製造方法に関する。 The present invention relates to a novel iron-copper (Fe-Cu) alloy based on iron (Fe) and containing an appropriate amount of copper (Cu). More specifically, the present invention has excellent mechanical properties while having high thermal conductivity. The present invention relates to an iron-copper alloy having electromagnetic wave shielding properties and soft magnetism, and a method for producing the same.
金属関連製造産業において、鉄鋼材料はアルミニウム合金のような軽量材料に取り替えられている。アルミニウム合金は、軽量性のみならず、熱伝導性、耐食性及び軟性などが優れて各種の産業分野で様々な用途として幅広く用いられている。アルミニウム合金は高い熱伝導性で熱を迅速に冷却させて成形品の変形と撓みを最小化することができる。これにより、アルミニウム合金は射出形成やダイカスト(die casting)用の金型素材として有用に用いられている。 In the metal-related manufacturing industry, steel materials are being replaced by lightweight materials such as aluminum alloys. Aluminum alloys are not only lightweight, but also have excellent thermal conductivity, corrosion resistance, and softness, and are widely used in various industrial fields for various purposes. Aluminum alloys have high thermal conductivity and can quickly cool heat to minimize deformation and deflection of the part. As a result, the aluminum alloy is usefully used as a mold material for injection molding and die casting.
例えば、韓国公開特許公報第10−2015−0046014号及び韓国登録特許公報第10−1606525号などにはダイカスト用のアルミニウム合金に関する技術が開示されている。アルミニウム合金はアルミニウム(Al)をベースとして、少量のシリコン(Si)、鉄(Fe)、マンガン(Mn)、及びマグネシウム(Mg)などを含有しており、アルミニウム−シリコン−マグネシウム(Al−Si−Mg)状の合金がダイカスト用の金型素材として多く用いられている。 For example, Korean Patent Publication No. 10-2015-0046014 and Korean Registered Patent Publication No. 10-1606525 disclose techniques related to aluminum alloys for die casting. The aluminum alloy is based on aluminum (Al) and contains a small amount of silicon (Si), iron (Fe), manganese (Mn), magnesium (Mg), etc., and is aluminum-silicon-magnesium (Al-Si-). Mg) -like alloys are often used as mold materials for die casting.
しかしながら、アルミニウム合金は強度及び耐磨耗性などの機械的な物性が低い。これに対して、高い熱伝導性及び耐食性を有するのみならず、強度及び耐摩耗性などの機械的な物性の優れたベリリウム−銅(Be−Cu)合金が金型素材としてスポットライトを浴びている。例えば、日本公開特許公報JP2003−003246号、韓国公開特許公報第10−2012−0048287号、韓国公開特許公報第10−2015−0053814号などには、ベリリウム−銅(Be−Cu)合金に関する技術が開示されている。 However, aluminum alloys have low mechanical properties such as strength and abrasion resistance. On the other hand, a beryllium-copper (Be-Cu) alloy, which not only has high thermal conductivity and corrosion resistance but also has excellent mechanical properties such as strength and wear resistance, is in the spotlight as a mold material. There is. For example, Japanese Patent Publication No. JP2003-003246, Korean Patent Publication No. 10-2012-0048287, Korean Patent Publication No. 10-2015-0053814, etc. describe techniques related to beryllium-copper (Be-Cu) alloys. It is disclosed.
ベリリウム−銅(Be−Cu)合金は、高強度及び高熱伝導性などを有する実用合金であって、これはダイカスト用の金型素材などとして有用である。ベリリウム−銅(Be−Cu)合金は、多くの場合、べリリウム(Be)と銅(Cu)を溶解鋳造した後、熱間や零間による塑性加工と焼鈍処理を繰り返す方法により得られ、機械的な物性の向上のためのコバルト(Co)が加えられている。しかしながら、ベリリウム−銅(Be−Cu)合金は連続鋳造が困難であり、ベリリウム(Be)と銅(Cu)の原料が高コストなので、経済性が良くない問題点がある。これにより、ベリリウム−銅(Be−Cu)合金は高コストにより高級製品に制限的に用いられて汎用性が劣るという問題点がある。 The beryllium-copper (Be-Cu) alloy is a practical alloy having high strength and high thermal conductivity, and is useful as a mold material for die casting and the like. Beryllium-copper (Be-Cu) alloys are often obtained by melting and casting beryllium (Be) and copper (Cu), and then repeating hot or zero plastic working and annealing. Cobalt (Co) is added to improve the physical properties. However, the beryllium-copper (Be-Cu) alloy is difficult to continuously cast, and the raw materials of beryllium (Be) and copper (Cu) are expensive, so that there is a problem that the economy is not good. As a result, the beryllium-copper (Be-Cu) alloy has a problem that it is limitedly used in high-class products due to high cost and is inferior in versatility.
本発明は、既存のベリリウム−銅(Be−Cu)合金を取り替える新規な鉄系合金組成であって、改善された特性を有する鉄−銅(Fe−Cu)合金、その製造方法、及び用途を提供することをその目的とする。 The present invention is a novel iron-based alloy composition that replaces an existing beryllium-copper (Be-Cu) alloy, and uses an iron-copper (Fe-Cu) alloy having improved properties, a method for producing the same, and an application thereof. Its purpose is to provide.
詳しくは、本発明は、鉄(Fe)をベースとし適量の銅(Cu)を含んで高い熱伝導性及び機械的な物性を有すると共に、電磁気波遮蔽性及び軟磁性などを有する鉄−銅(Fe−Cu)合金及びその製造方法を提供することを目的とする。また、本発明は、前記鉄−銅(Fe−Cu)合金の用途として、前記鉄−銅(Fe−Cu)合金を含む素材を提供することを目的とする。 Specifically, the present invention is based on iron (Fe), contains an appropriate amount of copper (Cu), has high thermal conductivity and mechanical properties, and has electromagnetic wave shielding property and soft magnetism. It is an object of the present invention to provide a Fe—Cu) alloy and a method for producing the same. Another object of the present invention is to provide a material containing the iron-copper (Fe-Cu) alloy as an application of the iron-copper (Fe-Cu) alloy.
前記目的を達成するために本発明は、鉄55〜95原子%と、銅5〜45原子%と、を含むことを特徴とする鉄−銅合金を提供する。 In order to achieve the above object, the present invention provides an iron-copper alloy comprising 55 to 95 atomic% of iron and 5 to 45 atomic% of copper.
さらに、本発明は、鉄80.5〜95原子%と、銅5〜19.5原子%と、を含み、下記(a)乃至(c)の物性を有することを特徴とする鉄−銅合金を提供する。
(a) 熱伝導率70W/m・K以上
(b) 引張強度300N/mm2以上
(c) 硬度100HB以上
Further, the present invention is an iron-copper alloy containing 80.5 to 95 atomic% of iron and 5 to 19.5 atomic% of copper and having the following physical properties (a) to (c). I will provide a.
(A) Thermal conductivity 70 W / m · K or more (b) Tensile strength 300 N / mm 2 or more (c) Hardness 100 HB or more
例示的な実施形態に従って、本発明による鉄−銅合金は球形の粒子状であり、0.1〜150μmのサイズを有することができる。 According to an exemplary embodiment, the iron-copper alloy according to the invention is in the form of spherical particles and can have a size of 0.1 to 150 μm.
さらに、本発明は、溶解炉を用意する第1工程と、鉄−銅合金に鉄55〜95原子%と、銅5〜45原子%とを含むように、前記溶解炉に鉄と銅を投入、溶解して溶湯を形成する第2工程と、前記溶湯を安定化する第3工程と、前記安定化した溶湯を鋳造型に注入して鋳造する第4工程と、を含むことを特徴とする鉄−銅合金の製造方法を提供する。 Further, in the present invention, the first step of preparing a melting furnace and iron and copper are charged into the melting furnace so that the iron-copper alloy contains 55 to 95 atomic% of iron and 5 to 45 atomic% of copper. It is characterized by including a second step of melting to form a molten metal, a third step of stabilizing the molten metal, and a fourth step of injecting the stabilized molten metal into a casting mold and casting. A method for producing an iron-copper alloy is provided.
一実施形態に従って、本発明による鉄−銅合金の製造方法は、前記第4工程を通じて得られた鋳造物を再溶解した後、噴射させて粉末状の鉄−銅合金粒子を得る第5工程をさらに含む。 According to one embodiment, the method for producing an iron-copper alloy according to the present invention comprises a fifth step of redissolving the casting obtained through the fourth step and then injecting the casting to obtain powdered iron-copper alloy particles. Including further.
好ましい実施形態に従って、前記第1工程は溶解炉の内面に多孔性の不純物吸収層を形成する表面処理段階を含む。この際、前記多孔性の不純物吸収層は、ケイ酸ジルコニウム(Zirconium Silicate)を含むことがよい。 According to a preferred embodiment, the first step comprises a surface treatment step of forming a porous impurity absorbing layer on the inner surface of the melting furnace. At this time, the porous impurity absorbing layer may contain zirconium silicate.
本発明の実施形態によれば、既存のベリリウム−銅(Be−Cu)合金を取り替える新規な鉄系合金を提供する。本発明は、鉄(Fe)に適量の銅(Cu)が溶融合金された非晶質の完全な合金であって、熱伝導性及び機械的な物性などが優れ、高い生産性及び経済性を有する鉄−銅合金を提供する効果がある。また、本発明は、高い熱伝導性と共に電磁気波遮蔽性及び軟磁性などを有し、金型素材のみならず、電子部品及び機械部品などとして汎用的に用いられる記鉄−銅合金を提供する効果がある。 According to an embodiment of the present invention, there is provided a novel iron-based alloy that replaces an existing beryllium-copper (Be-Cu) alloy. The present invention is an amorphous complete alloy in which an appropriate amount of copper (Cu) is melt-alloyed with iron (Fe), and has excellent thermal conductivity and mechanical properties, and is highly productive and economical. It has the effect of providing an iron-copper alloy. The present invention also provides an iron-copper alloy that has high thermal conductivity, electromagnetic wave shielding property, soft magnetism, etc., and is widely used not only as a mold material but also as an electronic part, a mechanical part, and the like. effective.
本発明において用いられる用語“及び/又は”はその前後に並べた構成要素のうち、少なくとも一つ以上を含むことをいう。本発明において用いられる用語“一つ以上”は一つまたは二つ以上の複数をいう。 The term "and / or" used in the present invention means that the term "and / or" includes at least one of the components arranged before and after the term. The term "one or more" used in the present invention refers to one or more or more.
本発明は、第1形態に従って、鉄(Fe)を主成分とする鉄系合金であって、新規な合金組成を有する鉄−銅合金を提供する。本発明は、第2形態に従って、前記鉄−銅合金の合金製造方法を提供する。また、本発明は、第3形態に従って、前記鉄−銅合金の用途として、前記鉄−銅合金を少なくとも含む素材を提供する。前記素材は、例えば、金型素材及び3Dプリンター用の素材などから選ばれることができる。 The present invention provides an iron-copper alloy which is an iron-based alloy containing iron (Fe) as a main component and has a novel alloy composition according to the first embodiment. The present invention provides an alloy production method for the iron-copper alloy according to the second embodiment. The present invention also provides a material containing at least the iron-copper alloy as an application of the iron-copper alloy according to the third embodiment. The material can be selected from, for example, a mold material, a material for a 3D printer, and the like.
本発明による鉄−銅合金は、鉄(Fe)と銅(Cu)を含み、銅(Cu)より鉄(Fe)の含量が高い鉄系合金であって、鉄(Fe)と銅(Cu)の全体基準として鉄(Fe)55〜95原子%(atomic %)と銅(Cu)5〜45原子%(atomic %)のとを含む。本発明において用いられる含量単位“原子%”は鉄(Fe)と銅(Cu)の原子(atoms)全体(FeとCuとの和)を基準としたのであり、これは当該業界において周知されたように、“体積%”とも表現され得る。即ち、本発明によいて、原子%は体積%とも表現されることができる。 The iron-copper alloy according to the present invention is an iron-based alloy containing iron (Fe) and copper (Cu) and having a higher iron (Fe) content than copper (Cu), and is iron (Fe) and copper (Cu). As an overall standard, iron (Fe) 55-95 atomic% (atomic%) and copper (Cu) 5-45 atomic% (atomic%) are included. The content unit "atomic%" used in the present invention is based on the entire atomic (atoms) of iron (Fe) and copper (Cu) (sum of Fe and Cu), which is well known in the industry. As such, it can also be expressed as "volume%". That is, according to the present invention, atomic% can also be expressed as volume%.
好ましい実施形態に従って、本発明による鉄−銅合金は鉄と銅以外の他の金属元素は含まない。また、本発明による鉄−銅合金は不可避な不純物として炭素(C)や酸素(O)などの不純物を含むことがあるが、このような不純物は極少量に過ぎない。不純物は、例えば、0.1原子%(0.1体積%)以下又は0.01原子%以下であって、不可避に含まれる。 According to a preferred embodiment, the iron-copper alloy according to the invention is free of metal elements other than iron and copper. Further, the iron-copper alloy according to the present invention may contain impurities such as carbon (C) and oxygen (O) as unavoidable impurities, but such impurities are only a very small amount. The impurities are, for example, 0.1 atomic% (0.1% by volume) or less or 0.01 atomic% or less, and are inevitably contained.
本発明による鉄−銅合金は鉄に適量の銅を含ませて鉄の利点と銅の利点を組み合わせて改善した特性を有する。本発明による鉄−銅合金は、少なくとも高い熱伝導性及び機械的な物性などを有する。具体的に、既存の鉄合金に比べて高い熱伝導性及び弾性などを有する。また、既存の銅合金に比べて、高い硬度及び耐磨耗性などを有する。さらに、低コストの鉄をベース(主成分)として高い経済性があり、鉄と銅の適定な組成(含量)により電磁気波遮蔽性及び軟磁性などをもち、様々な用途としても用いられることができる。例えば、ソレノイドなどの精密部品、電磁気波遮蔽材及び3Dプリンター用の素材としても使用が可能である。 The iron-copper alloy according to the present invention has improved properties by incorporating an appropriate amount of copper into iron and combining the advantages of iron and the advantages of copper. The iron-copper alloy according to the present invention has at least high thermal conductivity and mechanical properties. Specifically, it has higher thermal conductivity and elasticity than existing iron alloys. In addition, it has higher hardness and abrasion resistance than existing copper alloys. Furthermore, it is highly economical based on low-cost iron (main component), has electromagnetic wave shielding properties and soft magnetism due to the appropriate composition (content) of iron and copper, and can be used for various purposes. Can be done. For example, it can be used as a precision component such as a solenoid, an electromagnetic wave shielding material, and a material for a 3D printer.
以下、本発明による鉄−銅合金の製造方法を説明しながら、本発明による鉄−銅合金の実施形態を説明する。以下後述する製造方法は、本発明による鉄−銅合金の製造を容易に具現する。しかしながら、本発明による鉄−銅合金は、後述する製造方法により製造されるものに限定されない。 Hereinafter, embodiments of the iron-copper alloy according to the present invention will be described while explaining the method for producing the iron-copper alloy according to the present invention. The production method described below easily embodies the production of the iron-copper alloy according to the present invention. However, the iron-copper alloy according to the present invention is not limited to those produced by the production method described later.
本発明による鉄−銅合金の製造方法(以下、“製造方法”と略称する)は、溶解炉を用意する第1工程、前記溶解炉に鉄と銅を投入、溶解して溶湯を形成する第2工程、前記溶湯を安定化させる第3工程、及び前記安定化した溶湯を鋳造型に注入して鋳造する第4工程と、を含む。また、本発明による製造方法は、選択的な工程として、前記第4工程を通じて得られた鋳造物から粉末状の鉄−銅合金粒子を得る第5工程をさらに含むことができる。各工程別の実施形態を説明すると、次の通りである。 The method for producing an iron-copper alloy according to the present invention (hereinafter, abbreviated as "manufacturing method") is the first step of preparing a melting furnace, the first step of putting iron and copper into the melting furnace and melting them to form a molten metal. It includes two steps, a third step of stabilizing the molten metal, and a fourth step of injecting the stabilized molten metal into a casting mold and casting. In addition, the production method according to the present invention can further include, as a selective step, a fifth step of obtaining powdered iron-copper alloy particles from the casting obtained through the fourth step. An embodiment for each process will be described as follows.
[1]溶解炉の準備(第1工程) [1] Preparation of melting furnace (first step)
上述したように、本発明による鉄−銅合金は鉄55〜95原子%と銅5〜45原子%を含む。本発明において特定する前記合金組成は理論的な溶融合金組成ではない。すなわち、鉄の含量が理論的に合金されうる量を超える比率である。このような合金組成は焼結による母合金の製造時には具現が可能であるが、溶解(溶湯)による溶融方法では、非晶質の完全な合金を得ることは困難である。一般に、鉄と銅は、銅より鉄の含量が低い場合(例えば、Fe含量2.5体積%未満)、溶融合金を得ることができる。しかしながら、本発明において特定する前記合金組成の場合には、溶湯でFe−rich相とCu−rich相との二相分離が発生し、偏析(ある一金属が一箇所に偏る)が発生して均一な分布の完全な溶融合金を得ることが困難である。 As mentioned above, the iron-copper alloy according to the present invention contains 55-95 atomic% iron and 5-45 atomic% copper. The alloy composition specified in the present invention is not a theoretical molten alloy composition. That is, the ratio of iron content exceeds the amount that can be theoretically alloyed. Such an alloy composition can be realized at the time of producing a mother alloy by sintering, but it is difficult to obtain an amorphous complete alloy by a melting method by melting (molten metal). In general, iron and copper can obtain a molten alloy when the iron content is lower than that of copper (for example, Fe content is less than 2.5% by volume). However, in the case of the alloy composition specified in the present invention, two-phase separation between the Fe-rich phase and the Cu-rich phase occurs in the molten metal, and segregation (one metal is biased to one place) occurs. It is difficult to obtain a perfect molten alloy with a uniform distribution.
本発明者は鉄の含量が高く完全な溶融合金を得るための各種の研究を繰り返した結果、銅の含量が適定で不純物の含量を最小化した場合及び/又は溶解過程を変化させた場合、偏析(偏重)無しに完全な溶融合金を得ることをわかった。本発明によれば、一つの実施形態に従って溶解炉の改善及び/又は溶解過程における原料投入方法を改善した場合、完全な溶融合金を得ることがわった。 As a result of repeating various studies to obtain a complete molten alloy with a high iron content, the present inventor found that the copper content was appropriate and the impurity content was minimized and / or the dissolution process was changed. , It was found that a complete molten alloy was obtained without segregation (uneven weight). According to the present invention, it has been found that a complete molten alloy is obtained when the melting furnace is improved and / or the raw material charging method in the melting process is improved according to one embodiment.
第1工程においては、上述した課題を解決するための一つの実施形態を提供する。第1工程によって、鉄と銅の溶湯を形成するための溶解炉を用意し、、前記溶解炉は急激な昇温により速い溶解が可能な高周波誘導熱の溶解炉を用いる。また、前記溶解炉はマグネシウムを主成分とするセラミック溶解炉を用いることがよい。前記セラミック溶解炉としては、例えば、酸化マグネシウムを主成分とするセラミックを高温、焼成を通じて製造したものを用いることができる。 In the first step, one embodiment for solving the above-mentioned problems is provided. A melting furnace for forming a molten metal of iron and copper is prepared by the first step, and the melting furnace uses a melting furnace of high-frequency induced heat capable of rapid melting by a rapid temperature rise. Further, the melting furnace may be a ceramic melting furnace containing magnesium as a main component. As the ceramic melting furnace, for example, a ceramic having magnesium oxide as a main component produced by firing at a high temperature can be used.
好ましい実施形態によって、前記溶解炉は内面に多孔性の不純物吸収層を形成させて用いる。詳しくは、第1工程は、高周波誘導熱のセラミック溶解炉を用意し、前記セラミック溶解炉の内面に多孔性の不純物吸収層を形成する表面処理段階を含む。この際、前記不純物吸収層は溶解炉の内面全体又は一部に形成され、具体的には、溶湯と当たる面である、溶解炉の少なくとも内部底面及び/又は壁体の内部面に形成されることができる。 According to a preferred embodiment, the melting furnace is used by forming a porous impurity absorbing layer on the inner surface. Specifically, the first step includes a surface treatment step of preparing a ceramic melting furnace having high frequency induced heat and forming a porous impurity absorption layer on the inner surface of the ceramic melting furnace. At this time, the impurity absorption layer is formed on the entire inner surface or a part of the melting furnace, and specifically, is formed on at least the inner bottom surface of the melting furnace and / or the inner surface of the wall body, which is the surface that comes into contact with the molten metal. be able to.
また、前記不純物吸収層は少なくとも不純物吸収剤を含む。詳しくは、前記表面処理段階では、不純物吸収剤、樹脂及び溶媒を含む吸収層組成物を溶解炉の内面に塗布した後、焼成して多孔性の不純物吸収層を形成することができる。本発明によれば、前記多孔性の不純物吸収層により、鉄−銅の溶湯内に含まれた不純物(例えば、C、Oなど)が吸収、除去されて、前記非理論的な合金の組成時にも偏析(偏重)無しに完全な合金を得ることができる。このような多孔性の不純物吸収層は、例えば、0.5〜2mmの厚さを有することがあるが、これに限定されない。 Further, the impurity absorbing layer contains at least an impurity absorbing agent. Specifically, in the surface treatment step, an absorption layer composition containing an impurity absorbing agent, a resin and a solvent can be applied to the inner surface of the melting furnace and then fired to form a porous impurity absorbing layer. According to the present invention, impurities (for example, C, O, etc.) contained in the molten iron-copper are absorbed and removed by the porous impurity absorbing layer during the composition of the non-theoretical alloy. A complete alloy can be obtained without segregation (uneven weight). Such a porous impurity absorbing layer may have, for example, a thickness of 0.5 to 2 mm, but is not limited thereto.
前記不純物吸収剤は、鉄−銅の溶湯内に含まれる不純物(例えは、C、Oなど)が吸収、除去できるものなら、特に限定されない。前記不純物吸収剤は粉末状であって、例えば、50〜500μmの大きさを有するものが用いられる。前記不純物吸収剤は金属酸化物及び/又は金属から選ばれるが、好ましくは、ケイ酸ジルコニウム(Zirconium Silicate)及びアルミニウム(Al)のうち選ばれた少なくとも一つ以上を含むことがよい。前記不純物吸収剤は、より好ましくは、ケイ酸ジルコニウムとアルミニウム(Al)の両方を用いることがよい。この際、前記アルミニウム(Al)は99.8重量%以上の高純度を有するものを用いることができる。前記不純物吸収剤としての前記ケイ酸ジルコニウムとアルミニウム(Al)は、他の金属酸化物や金属に比べて、溶湯内の不純物を完全に効果的に除去することができるので、本発明において好ましい。前記ケイ酸ジルコニウムとアルミニウム(Al)は、詳しくは、溶湯内の不純物を完全に除去して鉄と銅のみを含む高純度の合金溶湯を形成することができる。これは、以下の実施形態によっても確認が可能である。 The impurity absorber is not particularly limited as long as it can absorb and remove impurities (for example, C, O, etc.) contained in the molten iron-copper. The impurity absorbent is in the form of powder, and for example, one having a size of 50 to 500 μm is used. The impurity absorber is selected from metal oxides and / or metals, but preferably contains at least one selected from zirconium silicate and aluminum (Al). More preferably, both zirconium silicate and aluminum (Al) may be used as the impurity absorbent. At this time, the aluminum (Al) having a high purity of 99.8% by weight or more can be used. The zirconium silicate and aluminum (Al) as the impurity absorbent are preferable in the present invention because they can completely and effectively remove impurities in the molten metal as compared with other metal oxides and metals. More specifically, the zirconium silicate and aluminum (Al) can completely remove impurities in the molten metal to form a high-purity alloy molten metal containing only iron and copper. This can also be confirmed by the following embodiments.
さらに、前記樹脂は接着性を有するものなら、特に限定されず、粉末状の不純物吸収剤の相互間を結集させながら、溶解炉の内面と不純物吸収層との初期接着力を提供できるものなら、いずれもよい。さらに、前記樹脂は焼成による高温の熱により除去され、不純物吸収層に多孔性を与える。前記樹脂は合成樹脂及び/又は天然樹脂などから選ばれることができる。前記樹脂は固状及び/又は液状となり得、例えば、アクリル系、ビニル系、エポキシ系、ウレタン系、シリコン系、オレフィン系、エステル系及びゴム系などから選ばれたいずれか一つ以上の重合体及び/又はこれらの共重合体などから選ばれることができる。 Further, the resin is not particularly limited as long as it has adhesiveness, as long as it can provide the initial adhesive force between the inner surface of the melting furnace and the impurity absorbing layer while concentrating the powdered impurity absorbing agents with each other. Both are good. Further, the resin is removed by high-temperature heat generated by firing to give the impurity absorbing layer porosity. The resin can be selected from synthetic resins and / or natural resins and the like. The resin can be solid and / or liquid, and is, for example, any one or more polymers selected from acrylic, vinyl, epoxy, urethane, silicon, olefin, ester, rubber and the like. And / or can be selected from these copolymers and the like.
前記樹脂は、好ましくは、ブタジエン−スチレン−アルキルメタクリレート共重合体(Butadiene−Styrene−Alkyl Methacrylate copolymer)を用いることができる。前記ブタジエン−スチレン−アルキルメタクリレート共重合体は、具体的な例として、ブタジエン−スチレン−メチルメタクリレート共重合体、ブタジエン−スチレン−エチルメタクリレート共重合体及び/又はブタジエン−スチレン−ブチルメタクリレート共重合体などから選ばれることができる。一例として、前記ブタジエン−スチレン−アルキルメタクリレート共重合体は50nm〜500nmの粒子サイズを有するものを用いることができる。このように樹脂として、ブタジエン−スチレン−アルキルメタクリレート共重合体を選び、ナノサイズを有するものを使用する場合、この樹脂が焼成により迅速に除去されることができ、粉末状の不純物吸収剤の間に均一に分散される。従って、不純物吸収剤間の結集力を改善するのみならず、不純物吸収層に均質かつ微細な多孔構造を形成させて不純物の吸収除去能が向上される。 As the resin, a butadiene-styrene-alkyl methacrylate copolymer (Butadie-Styrene-Alkyl Methacrylate copolymer) can be preferably used. Specific examples of the butadiene-styrene-alkyl methacrylate copolymer include a butadiene-styrene-methyl methacrylate copolymer, a butadiene-styrene-ethyl methacrylate copolymer and / or a butadiene-styrene-butyl methacrylate copolymer. Can be selected from. As an example, the butadiene-styrene-alkyl methacrylate copolymer having a particle size of 50 nm to 500 nm can be used. As described above, when a butadiene-styrene-alkyl methacrylate copolymer is selected as the resin and a nano-sized resin is used, this resin can be quickly removed by firing, and between powdered impurity absorbers. Is evenly distributed. Therefore, not only the gathering force between the impurity absorbing agents is improved, but also the ability to absorb and remove impurities is improved by forming a homogeneous and fine porous structure in the impurity absorbing layer.
前記溶媒は分散性と塗布性のためのものであって、炭化水素系から選ばれることができる。前記溶媒は、例えば、アルコール類及び/又はケトン類などから選ばれることができる。 The solvent is for dispersibility and coatability and can be selected from hydrocarbon systems. The solvent can be selected from, for example, alcohols and / or ketones.
さらに、前記吸収層組成物は一例として不純物吸収剤50〜80重量%、樹脂5〜20重量%、及び溶媒15〜40重量%を含むことができる。この際、不純物吸収剤の含量が50重量%未満である場合、不純物の吸収除去能が減少することがあり、80重量%を超える場合、多孔性と塗布性が低下することもある。また、前記樹脂の含量が5重量%未満である場合、多孔性と接着性が低下することがあり、20重量%を超える場合、相対的に不純物吸収剤の含量が減って不純物の吸収除去能が減少することもある。また、溶媒は分散性と塗布性を考慮して上述した範囲がよい。 Further, the absorption layer composition can contain, for example, 50 to 80% by weight of the impurity absorbent, 5 to 20% by weight of the resin, and 15 to 40% by weight of the solvent. At this time, if the content of the impurity absorbent is less than 50% by weight, the ability to absorb and remove impurities may decrease, and if it exceeds 80% by weight, the porosity and coatability may decrease. Further, when the content of the resin is less than 5% by weight, the porosity and adhesiveness may decrease, and when it exceeds 20% by weight, the content of the impurity absorber is relatively reduced and the ability to absorb and remove impurities. May decrease. Further, the solvent is preferably in the above range in consideration of dispersibility and coatability.
上述したように第1工程を通じて溶解炉の内面に多孔性の不純物吸収層を形成した場合、溶解過程で溶湯内に含まれれる不純物が吸収、除去されて均質状の完全な鉄−銅合金を生成することができると共に、不純物をほとんど含まない高純度の鉄−銅合金を効果的に得ることができる。 As described above, when a porous impurity absorption layer is formed on the inner surface of the melting furnace through the first step, impurities contained in the molten metal are absorbed and removed during the melting process to obtain a homogeneous iron-copper alloy. It can be produced and a high-purity iron-copper alloy containing almost no impurities can be effectively obtained.
[2]溶解(第2工程) [2] Dissolution (second step)
前記溶解炉に鉄と銅の合金原料を投入する。この際、鉄は高純度の純鉄を用いることができ、前記銅は高純度の電解銅を用いることができる。溶解炉は電源の印加による高周波誘導熱により加温されうる。溶解炉は、鉄と銅の溶解可能温度で維持するとよい。例えば、高周波誘導熱を通じて溶解炉を迅速に昇温させて約1520〜1650℃で維持して鉄と銅を溶解することがよい。このような溶解過程においては、攪拌が行われることができる。 An alloy raw material of iron and copper is put into the melting furnace. At this time, high-purity pure iron can be used as the iron, and high-purity electrolytic copper can be used as the copper. The melting furnace can be heated by high frequency induced heat by applying a power source. The melting furnace should be maintained at a melting temperature of iron and copper. For example, it is preferable to rapidly raise the temperature of the melting furnace through high-frequency induced heat and maintain it at about 152 to 1650 ° C. to melt iron and copper. In such a dissolution process, stirring can be performed.
さらに、第2工程においては、最終生成された鉄−銅合金の全体を基準として鉄55〜95原子% (又は体積%)と銅5〜45原子%(又は体積%)を含むように、前記溶解炉に鉄と銅を投入、溶解して溶湯を形成する。詳しくは、溶解炉に鉄と銅の総投入量を鉄55〜95体積%と銅5〜45体積%(即ち、鉄:銅=55〜95:5〜45の体積比)とする場合、前記合成組成を有するようにすることができる。この際、銅の含量が5原子%(5体積%)未満の場合、例えば、熱伝導性、耐食性及び/又は電磁気波遮蔽性などがわずかになることがある。また、銅の含量が45原子%(45体積%)を超える場合、相対的に鉄の含量が減り、例えば、硬度及び/又は耐磨耗性などの機械的強度が低下することかある。 Further, in the second step, iron 55 to 95 atomic% (or volume%) and copper 5 to 45 atomic% (or volume%) are contained based on the whole of the finally produced iron-copper alloy. Iron and copper are put into the melting furnace and melted to form a molten metal. Specifically, when the total amount of iron and copper input to the melting furnace is 55 to 95% by volume of iron and 5 to 45% by volume of copper (that is, the volume ratio of iron: copper = 55 to 95: 5 to 45), the above. It can have a synthetic composition. At this time, if the copper content is less than 5 atomic% (5% by volume), for example, thermal conductivity, corrosion resistance and / or electromagnetic wave shielding property may be slight. Further, when the copper content exceeds 45 atomic% (45% by volume), the iron content may be relatively reduced, and for example, mechanical strength such as hardness and / or abrasion resistance may be reduced.
本発明の好ましい実施形態に従って、上述した点を考慮して、第2工程においては、最終生成された鉄−銅合金の全体を基準として鉄80.5〜95原子%と銅5〜19.5原子%を含むように、前記溶解炉に鉄と銅を投入、溶解して溶湯を形成することがよい。即ち、溶解炉に鉄と銅の総投入量を鉄80.5〜95体積%と銅5〜19.5体積%(即ち、鉄:銅=80.5〜95:5〜19.5の体積比)とする場合、前記合成組成を有するようにすることが好ましい。このような好ましい合金組成を有する場合、優れた熱伝導性、機械的な物性、電磁気波遮蔽性及び/又は軟磁性などを有する。 In accordance with the preferred embodiment of the present invention, in consideration of the above points, in the second step, 80.5 to 95 atomic% of iron and 5 to 19.5 copper are used as a reference for the entire iron-copper alloy finally produced. It is preferable to put iron and copper into the melting furnace and melt them to form a molten metal so as to contain atomic%. That is, the total amount of iron and copper input to the melting furnace is 80.5 to 95% by volume of iron and 5 to 19.5% by volume of copper (that is, iron: copper = 80.5 to 95: 5 to 19.5). Ratio), it is preferable to have the synthetic composition. When having such a preferable alloy composition, it has excellent thermal conductivity, mechanical properties, electromagnetic wave shielding property and / or soft magnetism.
一実施形態に従って、前記溶解炉に鉄と銅を投入するときに、鉄と銅を初期に1:1の体積比で投入し、攪拌をしながら迅速に溶解させた後、鉄を追加に投入して前記合金組成を有するようにすることができる。即ち、一回の投入によって前記合成組成を有させることより、初期に鉄と銅を1:1の体積比で投入し、その後、鉄を追加に投入することにより、前記合金組成を有するようにすることが均質な鉄−銅の合金組成に好ましい。さらに、鉄の追加投入時には間欠的に少しずつ投入することがより好ましい。即ち、少量で数回にかけて鉄を追加投入することが均質な合金組成に有利である。 According to one embodiment, when iron and copper are charged into the melting furnace, iron and copper are initially charged in a volume ratio of 1: 1 and rapidly melted with stirring, and then iron is additionally charged. It is possible to have the alloy composition. That is, since the synthetic composition is provided by a single charge, iron and copper are initially charged at a volume ratio of 1: 1 and then iron is additionally charged so as to have the alloy composition. Preferably for a homogeneous iron-copper alloy composition. Further, it is more preferable to add iron little by little intermittently. That is, it is advantageous for a homogeneous alloy composition to additionally add iron in a small amount several times.
また、第2工程(溶解過程)においては、溶解炉に通常のように脱酸剤を添加して脱酸(酸化防止)させながら工程を行わせる。さらに、第2工程(溶解過程)においては、通常のようにフラックスをさらに添加することができる。この際、前記脱酸剤とフラックスは通常用いられるものを用いることができる。前記脱酸剤は、例えば、99.8重量%以上の高純度Al及び/又は高純度Tiなどを用いることができ、前記フラックスはAl2O3、CaO及び/又はSiO2などを用いることができる。 Further, in the second step (dissolution process), a deoxidizing agent is added to the melting furnace as usual to deoxidize (antioxidize) the process. Further, in the second step (dissolving process), the flux can be further added as usual. At this time, the deoxidizer and the flux which are usually used can be used. As the deoxidizer, for example, 99.8% by weight or more of high-purity Al and / or high-purity Ti can be used, and as the flux, Al 2 O 3 , Ca O and / or SiO 2 or the like can be used. it can.
[3]安定化(第3工程) [3] Stabilization (third step)
前記溶解によって生成された溶湯を安定化させる。安定化は溶解炉の電源供給を遮断し、溶湯を溶解路に所定の時間放置する方法で行われることができる。この際、安定化は、溶湯の温度を、例えば、1450〜1520℃で維持して放置する方法によって行われることができる。このような安定化によって、鉄と銅の均質化が行われることができる。 The molten metal produced by the dissolution is stabilized. Stabilization can be performed by cutting off the power supply of the melting furnace and leaving the molten metal in the melting path for a predetermined time. At this time, stabilization can be performed by a method in which the temperature of the molten metal is maintained at, for example, 1450 to 1520 ° C. and left to stand. Such stabilization allows homogenization of iron and copper.
[4]鋳造(第4工程) [4] Casting (4th step)
前記安定化された溶湯を鋳造型に注入して一定な形態の合金鋳造物を鋳造する。第4工程(鋳造)は通常の工程に従う。前記鋳造型は特に限定されず、鋳塊(ingot)及び鋳造片の形状を有したり、場合によっては、実際の適用製品の形状を有することができる。さらに、前記鋳造型は通常のように冷却機能を有することができる。 The stabilized molten metal is injected into a casting mold to cast an alloy casting of a certain form. The fourth step (casting) follows a normal step. The casting mold is not particularly limited and may have the shape of an ingot and a cast piece, or in some cases, the shape of an actual applicable product. Further, the casting mold can have a cooling function as usual.
また、第4工程から得られた鋳造物は通常の熱処理及び/又は冷却などの工程によって後処理されうる。前記鋳造物は、具体例として、焼鈍(annealing)、焼ならし(normalizing)、焼入れ(quenching)及び/又は焼戻し(tempering)などの工程を通じて後処理されうる。このような後処理は適用用途及び製品によって適宜に選ばれることができる。例えば、機械的強度(引張強度及び硬度など)が求められる製品の場合、焼入れ及び焼戻しが行われる。さらに、前記鋳造物は再溶解及び/又は後加工を通じて様々な形状を有し、実際の適用製品や半製品などとして加工されうる。 In addition, the casting obtained from the fourth step can be post-treated by steps such as ordinary heat treatment and / or cooling. The casting may be post-processed, for example, through steps such as annealing, normalizing, quenching and / or tempering. Such post-treatment can be appropriately selected depending on the application and the product. For example, in the case of a product that requires mechanical strength (tensile strength, hardness, etc.), quenching and tempering are performed. Further, the casting has various shapes through redissolving and / or post-processing and can be processed as an actual applicable product, semi-finished product or the like.
[5]粒子化(第5工程) [5] Particle formation (fifth step)
第5工程は選択的な工程であって、これを通じて粉末状の鉄−銅合金を得ることができる。第5工程に従って、前記第4工程(鋳造)から得られた鋳造物を再溶解した後、噴射させて粉末状の鉄−銅合金粒子を得る。具体的に、第5工程は前記鋳造物を再溶解する再溶解段階と、前記再溶解された溶解物を噴射させて粉末状の鉄−銅粒子を得る粒子化段階と、を含むことができる。 The fifth step is a selective step through which a powdered iron-copper alloy can be obtained. According to the fifth step, the casting obtained from the fourth step (casting) is redissolved and then sprayed to obtain powdered iron-copper alloy particles. Specifically, the fifth step can include a re-dissolution step of redissolving the casting and a particleization step of injecting the redissolved solution to obtain powdered iron-copper particles. ..
この際、前記再溶解段階では第1工程でのような溶解炉を用いることができる。また、第5工程の再溶解段階では、鉄−銅合金の酸化を防止するために、真空の溶解炉で再溶解させることがよい。すなわち、溶解炉は真空炉を用いることができる。このような真空炉において、前記鋳造物を1600〜1700℃で再溶解させ得る。前記粒子化段階は再溶解された溶解物を1400〜1500℃で噴射して粉末状で粒子化することができる。この際、粒子化した粉末は、例えば、0.1〜150μmのサイズを有することができる。このように得られた粉末状の鉄−銅合金粒子は、好ましくは、球形の粒子状を有することができる。 At this time, in the remelting step, a melting furnace as in the first step can be used. Further, in the redissolving step of the fifth step, in order to prevent oxidation of the iron-copper alloy, it is preferable to redissolve in a vacuum melting furnace. That is, a vacuum furnace can be used as the melting furnace. In such a vacuum furnace, the casting can be redissolved at 1600 to 1700 ° C. In the particle formation step, the redissolved solution can be injected at 1400 to 1500 ° C. to form particles in the form of powder. At this time, the particleized powder can have a size of, for example, 0.1 to 150 μm. The powdery iron-copper alloy particles thus obtained can preferably have a spherical particle shape.
上述した本発明の製造方法によれば、鉄55〜95原子%と銅5〜45原子%を含む非理論的な合金組成であるが、偏析(偏重)なしに完全な合金を得ることができる。また、本発明によって製造された鉄−銅合金は鉄の利点と銅の利点とを適宜に合わせて、上述したような高い熱伝導性及び機械的な物性(引張強度、硬度及び耐摩耗性など)を有すると共に、電磁気波遮蔽性及び軟磁性などを有するので、各種の用途としても使用が可能である。 According to the production method of the present invention described above, although it is a non-theoretical alloy composition containing 55 to 95 atomic% of iron and 5 to 45 atomic% of copper, a complete alloy can be obtained without segregation (bias). .. Further, the iron-copper alloy produced by the present invention appropriately combines the advantages of iron and the advantages of copper, and has high thermal conductivity and mechanical properties (tensile strength, hardness, abrasion resistance, etc.) as described above. ), And also has electromagnetic wave shielding properties and soft magnetism, so it can be used for various purposes.
好ましい実施形態に従って、本発明による鉄−銅合金は鉄80.5〜95原子%(又は体積%)と銅5〜19.5原子%(又は体積%)を含む。より詳しくは、鉄82.5〜90.5原子%と銅9.5〜17.5原子%を含むことができる。このような合成組成を有する場合、熱伝導性、機械的な物性、電磁気波遮蔽性及び/又は軟磁性などの特性が効果的に改善される。 According to a preferred embodiment, the iron-copper alloy according to the invention comprises 80.5 to 95 atomic% (or volume%) of iron and 5 to 19.5 atomic% (or volume%) of copper. More specifically, it can contain 82.5 to 90.5 atomic% of iron and 9.5 to 17.5 atomic% of copper. With such a synthetic composition, properties such as thermal conductivity, mechanical properties, electromagnetic wave shielding and / or soft magnetism are effectively improved.
さらに、本発明による鉄銅合金は下記(a)乃至(c)の物性を有することがよい。下記(a)乃至(c)の物性を有する場合、射出成形及びダイカスト用などの金型素材のみならず、3Dプリンター用の素材として汎用的な使用が可能である。 Further, the iron-copper alloy according to the present invention may have the following physical properties (a) to (c). When it has the following physical characteristics (a) to (c), it can be used for general purposes not only as a mold material for injection molding and die casting, but also as a material for a 3D printer.
(a) 熱伝導率70W/m・K以上
(b) 引張強度300N/mm2以上
(c) 硬度100HB以上
(A) Thermal conductivity 70 W / m · K or more (b) Tensile strength 300 N / mm 2 or more (c) Hardness 100 HB or more
前記熱伝導率、引張強度及び硬度は通常の測定方法に基づいて測定される。熱伝導率は、例えば、ASTM E1461(Laser flash: Thru−plane)に準じて常温(20〜25℃)で測定された値となり得る。また、引張強度はKS B 0801に準じて測定され、硬度はKS B 0805に準じて測定された値となり得る。 The thermal conductivity, tensile strength and hardness are measured based on a usual measuring method. The thermal conductivity can be, for example, a value measured at room temperature (20 to 25 ° C.) according to ASTM E1461 (Laser flash: Thru-plane). Further, the tensile strength can be measured according to KS B 0801, and the hardness can be a value measured according to KS B 0805.
前記熱伝導率は、具体例として、70〜150W/m・Kを有することができる。また、前記引張強度は、具体例として、300〜1350N/mm2を有することができる。さらに、前記硬度は、ブリネル硬度(Brinell Hardness)であって、その具体例としては、100〜400HBを有することができる。上述した各物性は適用用度に従って最適化され得る。例えば、引張強度及び硬度の場合、上述したような後処理(焼ならし、焼入れ及び焼戻しなど)を通じて増えることがあり、このような後処理によって引張強度は500N/mm2以上、硬度は200HB以上を有することができる。 As a specific example, the thermal conductivity can have 70 to 150 W / m · K. Further, the tensile strength can have 300 to 1350 N / mm 2 as a specific example. Further, the hardness is Brinell Hardness, and as a specific example thereof, it can have 100 to 400 HB. Each of the above-mentioned physical properties can be optimized according to the applicability. For example, in the case of tensile strength and hardness, it may increase through post-treatment (normalizing, quenching, tempering, etc.) as described above, and such post-treatment results in a tensile strength of 500 N / mm 2 or more and a hardness of 200 HB or more. Can have.
例示的な実施形態に従って、本発明による鉄−銅合金は、前記(a)乃至(c)の物性ととも(d)45〜650mmの透磁率(magnetic permeability)を有することができる。前記透磁率は磁性体(金属など)に対する通常の測定方法に基づいて測定され、これは50Hzの低周波数で測定された値である。 According to an exemplary embodiment, the iron-copper alloy according to the present invention can have the physical properties of (a) to (c) and (d) a magnetic permeability of (d) 45 to 650 mm. The magnetic permeability is measured based on a usual measuring method for a magnetic material (metal or the like), which is a value measured at a low frequency of 50 Hz.
さらに、本発明による鉄−銅合金は球形の粒子状を有することが好ましい。球形の粒子状は第5工程によって具現が可能である。この際、本発明による鉄−銅合金は球形の粒子状として、例えば、0.1〜150μmの大きさを有することができる。このように、球形の粒子状である場合、3Dプリンター用の素材として有用に用いられることができる。本発明において、“球形”とは、完全な球形のみをいうのではなく、完全な球形(spherical)のみならず、準−球形(quasi−spherical)を含む。 Further, the iron-copper alloy according to the present invention preferably has a spherical particle shape. The spherical particle shape can be realized by the fifth step. At this time, the iron-copper alloy according to the present invention can have a size of, for example, 0.1 to 150 μm as spherical particles. As described above, when it is in the form of spherical particles, it can be usefully used as a material for a 3D printer. In the present invention, the term "spherical" includes not only a perfect sphere but also a quasi-spherical as well as a perfect sphere.
本発明において、“球形の粒子”は、鉄−銅の合金が非理論的な合金組成であっても、偏析(偏重)無しに鉄と銅が合金内に均一に分布し、完全な溶融合金がなされたことをいう。この点において、“球形の粒子”は技術的な意義を有する。即ち、完全な溶融合金がなされない場合、噴射を通じて球形の粒子状を有することが困難である。また、本発明において、“球形の粒子”は再溶解を通じて均一な組成の鉄−銅合金成形物が加工できるという点からも、技術的な意義を有する。 In the present invention, the "spherical particles" are completely molten alloys in which iron and copper are uniformly distributed in the alloy without segregation (eccentricity) even if the iron-copper alloy has a non-theoretical alloy composition. It means that it was done. In this respect, "spherical particles" have technical significance. That is, if a perfect molten alloy is not formed, it is difficult to have a spherical particle shape through injection. Further, in the present invention, the "spherical particles" have technical significance in that an iron-copper alloy molded product having a uniform composition can be processed through redissolving.
一方、本発明による鉄−銅合金は様々な分野及び用途として用いられることができ、適用分野及び用途は特に限定されない。本発明による鉄−銅合金は、上述したように、金型素材のみならず、電子部品、精密機械、高熱機械部品及び3Dプリンター用の素材などとしても用いられる。また、本発明による鉄−銅合金は、弾性材料、遮蔽材料、抗菌材料、センサ材料及び手術用の医療道具などのみならず、エネルギー分野や塗料分野などに広く適用されうる。 On the other hand, the iron-copper alloy according to the present invention can be used in various fields and uses, and the fields of application and uses are not particularly limited. As described above, the iron-copper alloy according to the present invention is used not only as a mold material, but also as a material for electronic parts, precision machines, high-temperature machine parts, 3D printers, and the like. Further, the iron-copper alloy according to the present invention can be widely applied not only to elastic materials, shielding materials, antibacterial materials, sensor materials and medical tools for surgery, but also to the energy field and the paint field.
以下、本発明の実施例及び比較例を例示する。下記の実施例は本発明の理解のために例示的に提供されるが、これにより本発明の技術的な範囲が限定することではない。また、下記の比較例は従来の技術を意味することではなく、ただ実施例と比較するために提供される。 Hereinafter, examples and comparative examples of the present invention will be illustrated. The following examples are provided exemplary for understanding the invention, but this does not limit the technical scope of the invention. Also, the comparative examples below do not imply conventional techniques, but are provided solely for comparison with the examples.
[実施例1] [Example 1]
<溶解炉> <Melting furnace>
高周波誘導熱溶解炉として、マグネシウムを主成分とするセラミック溶解炉を用意した。その後、用意した溶解炉の内部壁面と底に多孔性の不純物吸収層を形成した。前記多孔性の不純物吸収層は、組成物の全体重量を基準として不純物吸収剤65重量%、樹脂15重量%及び溶媒30重量%を混合した吸収層組成物を約1mmの厚さで塗布した後、約1150℃の温度で加熱、焼成して形成した。この際、前記不純物吸収剤としては、ケイ酸ジルコニウム(ZrSiO4)とアルミニウム(Al)粉末を用い、前記樹脂としては、ブタジエン−スチレン−メチルメタクリレート共重合体を用い、前記溶媒としては、イソプロピルアルコールを用いた。 As a high-frequency induction thermal melting furnace, a ceramic melting furnace containing magnesium as a main component was prepared. Then, a porous impurity absorption layer was formed on the inner wall surface and the bottom of the prepared melting furnace. The porous impurity absorbing layer is obtained by applying an absorbent layer composition in which 65% by weight of an impurity absorbing agent, 15% by weight of a resin and 30% by weight of a solvent are mixed with a thickness of about 1 mm based on the total weight of the composition. , Was formed by heating and firing at a temperature of about 1150 ° C. At this time, zirconium silicate (ZrSiO 4 ) and aluminum (Al) powder are used as the impurity absorber, butadiene-styrene-methylmethacrylate copolymer is used as the resin, and isopropyl alcohol is used as the solvent. Was used.
<溶湯/安定化/鋳造> <Melting / Stabilizing / Casting>
前記溶解炉に鉄(純度、約99.9重量%の純鉄)と銅(純度、約99.9重量%の電解銅)を初期に1:1の体積比で投入し攪拌をしながら、出力を高めて迅速に溶解させた。この際、溶解過程では脱酸剤(Al)を間欠的に添加して脱酸を行って進行させた。また、肉眼観察に通じて投入された鉄と銅の完全な溶解を確認した後、鉄の含量を高めるために溶解炉に鉄を少しずつ追加投入し、溶湯の温度約1550℃で完全に溶解させた。その後、溶解炉の電源を遮断し、溶湯の温度が約1500℃になるまで放置して安定化させた。次に、安定化した溶湯を鋳造型に注入した後、冷却させてFe−Cu合金鋳塊(ingot)を得た。 Iron (purity, about 99.9% by weight of pure iron) and copper (purity, about 99.9% by weight of electrolytic copper) were initially charged into the melting furnace at a volume ratio of 1: 1 while stirring. The output was increased and dissolved quickly. At this time, in the dissolution process, an antacid (Al) was intermittently added to deoxidize and proceed. In addition, after confirming the complete dissolution of the iron and copper added through macroscopic observation, iron was added little by little to the melting furnace to increase the iron content, and the iron was completely melted at a molten metal temperature of about 1550 ° C. I let you. Then, the power supply of the melting furnace was turned off, and the molten metal was allowed to stabilize until the temperature of the molten metal reached about 1500 ° C. Next, the stabilized molten metal was injected into the casting mold and then cooled to obtain an Fe—Cu alloy ingot.
[実施例2及び実施例3] [Example 2 and Example 3]
前記実施例1に比べて、最終合金組成(FeとCuの原子%)を異にするために、溶解過程において鉄の追加投入量を異に設定したことを除いては、実施例1と同様に実施して各実施例によるFe−Cu合金鋳塊(ingot)を得た。 Same as Example 1 except that the additional iron input amount was set differently in the melting process in order to make the final alloy composition (atomic% of Fe and Cu) different from that of Example 1. To obtain Fe—Cu alloy ingots according to each example.
[比較例1] [Comparative Example 1]
溶解炉の内面に多孔性の不純物吸収層を形成するのにおいて、不純物吸収剤の種類を異にしたことを除いては、実施例1と同様に実施した。具体的に、不純物吸収剤として、ケイ酸ジルコニウム(ZrSiO4)とアルミニウム(Al)の代わりに、酸化ジルコニウム(ZrO2)を用いたことを除いては、実施例1と同様に実施した。 In forming the porous impurity absorption layer on the inner surface of the melting furnace, the same procedure as in Example 1 was carried out except that the types of impurity absorbers were different. Specifically, the same procedure as in Example 1 was carried out except that zirconium oxide (ZrO 2 ) was used instead of zirconium silicate (ZrSiO 4 ) and aluminum (Al) as the impurity absorbent.
[比較例2] [Comparative Example 2]
前記実施例1に比べて、溶解炉に鉄と銅を投入するときに9:1の体積比で一回に投入し、また、溶解炉の内面には多孔性の不純物吸収層を形成せず溶解して製造されたものを比較例2による試片として用いた。 Compared to Example 1, when iron and copper were charged into the melting furnace, they were charged at a time at a volume ratio of 9: 1, and a porous impurity absorption layer was not formed on the inner surface of the melting furnace. The one produced by melting was used as a sample according to Comparative Example 2.
このように得られたFe−Cu合金試片に対して、次のように成分を分析し、その結果を[表1]に示した。また、各合金試片に対して、熱伝導率、引張強度、硬度及び透磁率(magnetic permeability)を評価し、その結果を次の[表1]に示した。熱伝導率は、金属試料の熱伝導度測定方法として、各合金試片の密度、比熱及び熱拡散係数を測定した後、ASTM E1461(Laser flash: Thru−plane)に準じて評価した。この際、すべてのテストは25℃の温度で行った。また、引張強度はKS B 0801に準じて評価し、硬度はKS B 0805に準じてブリネル硬度(Brinell Hardness)として評価した。さらに、透磁率は透磁率測定器(日本、理研電子(株)の製品、モデル名BHU−60)を用いて周波数50Hzで評価した。 The components of the Fe—Cu alloy specimen thus obtained were analyzed as follows, and the results are shown in [Table 1]. In addition, the thermal conductivity, tensile strength, hardness and magnetic permeability of each alloy sample were evaluated, and the results are shown in the following [Table 1]. The thermal conductivity was evaluated according to ASTM E1461 (Laser flash: Thru-plane) after measuring the density, specific heat and thermal diffusion coefficient of each alloy sample as a method for measuring the thermal conductivity of a metal sample. At this time, all tests were performed at a temperature of 25 ° C. The tensile strength was evaluated according to KS B 0801, and the hardness was evaluated as Brinell Hardness according to KS B 0805. Further, the magnetic permeability was evaluated at a frequency of 50 Hz using a magnetic permeability measuring device (product of Riken Denshi Co., Ltd., Japan, model name BHU-60).
<成分分析> <Component analysis>
重さを測定した合金試片をグラス(glass)材質のビーカーに入れ、王水(塩酸+硫酸水溶液)10mLを加えて溶解させた。下記の測定条件による高周波誘導結合プラズマ発光分光分析(ICP−AES)を通じてFeとCuを定量して試料中の濃度に換算して分析した。 The weighted alloy specimen was placed in a glass beaker, and 10 mL of aqua regia (hydrochloric acid + sulfuric acid aqueous solution) was added to dissolve it. Fe and Cu were quantified through high frequency inductively coupled plasma emission spectroscopy (ICP-AES) under the following measurement conditions and converted to concentrations in the sample for analysis.
*ICP−AESの測定条件
測定装置: PerkinElmer Optima 5300DV
測定波長: 238.204nm(Fe), 327.398nm(Cu)
定量方法: 内部標準法
* ICP-AES measurement conditions Measuring device: PerkinElmer Optima 5300DV
Measurement wavelength: 238.204 nm (Fe), 327.398 nm (Cu)
Quantitative method: Internal standard method
しかしながら、比較例1及び2の場合、完全な合金が行われなく、偏析が発生することがわかる。また、引張強度の測定時、偏析によりクラックが発生して引張強度の測定が不可能であった。さらに、比較例1及び2の場合、偏析により成分が不均一になるので、正確な評価が困難で[表1]に表記しなかった。硬度及び透磁率の場合にも同様な理由から表記しなかった。 However, in the case of Comparative Examples 1 and 2, it can be seen that the complete alloy is not formed and segregation occurs. In addition, when measuring the tensile strength, cracks were generated due to segregation, making it impossible to measure the tensile strength. Further, in the cases of Comparative Examples 1 and 2, since the components became non-uniform due to segregation, accurate evaluation was difficult and not shown in [Table 1]. Hardness and magnetic permeability are not shown for the same reason.
下記の[表2]は後処理による物性評価結果であって、これは前記実施例2と同じ合金試片に対して処理前と処理後の結果を示したものである。後処理は通常的な方向に従って、焼鈍(annealing)、焼ならし(normalizing)、焼入れ(quenching)、及び焼戻し(tempering)を行った。 The following [Table 2] shows the results of evaluation of physical properties by post-treatment, which show the results before and after treatment for the same alloy sample as in Example 2. The post-treatment was annealing, normalizing, quenching, and tempering according to the usual directions.
前記[表2]に示したように、Fe−Cu合金は後処理により物性が変わることがわかる。例えば、温度1050℃で焼入れ(及び焼戻し)を行った場合、1300N/mm2以上の引張強度と370HB以上の硬度であって、処理前に比べて機械的な強度が向上したことがわかる。このように純粋単一金属(純鉄など)のように熱処理によって機械的強度が向上したことから、これは完全な合金がなされたことを意味する。 As shown in [Table 2] above, it can be seen that the physical characteristics of the Fe—Cu alloy change depending on the post-treatment. For example, when quenching (and tempering) was performed at a temperature of 1050 ° C., the tensile strength was 1300 N / mm 2 or more and the hardness was 370 HB or more, and it can be seen that the mechanical strength was improved as compared with that before the treatment. This means that a complete alloy was formed because the mechanical strength was improved by the heat treatment like a pure single metal (pure iron, etc.).
[実施例4〜6] [Examples 4 to 6]
上述した実施例1に比べて、最終合金組成(FeとCuの原子%)を異に設定するために、溶解過程において鉄の追加投入量を異にしたことを除いては、実施例1と同様な方法で実施して各実施例(4〜6)によるFe−Cu合金鋳塊(ingot)を得た。また、本実施例においては鋳造によって得られたFe−Cu合金鋳塊を次のように粒子化させて粉末状のFe−Cu合金粒子を製造した。 Compared to Example 1 described above, except that the amount of additional iron input was different in the melting process in order to set the final alloy composition (atomic% of Fe and Cu) differently from Example 1. The same method was carried out to obtain Fe—Cu alloy ingots according to each of Examples (4 to 6). Further, in this example, the Fe—Cu alloy ingot obtained by casting was pulverized as follows to produce powdered Fe—Cu alloy particles.
まず、鋳造によって得られた各実施例(4〜6)によるFe−Cu合金鋳塊を高周波誘導熱の溶解炉に入れ、最大出力を加えて約1650℃の温度で再溶解させた。この際、溶解炉は酸化防止のために真空状態を維持した。その後、噴射機を用いて前記再溶解された溶解物を噴射させて粒子化させた。この際、噴射チャンバーは酸化防止のためにアルゴン(Ar)ガス雰囲気で維持し、前記溶解物を1450℃の温度で噴射させて製造した。 First, the Fe—Cu alloy ingots according to each of Examples (4 to 6) obtained by casting were placed in a melting furnace of high-frequency induced heat and redissolved at a temperature of about 1650 ° C. by applying maximum output. At this time, the melting furnace was maintained in a vacuum state to prevent oxidation. Then, the redissolved solution was injected using an injector to form particles. At this time, the injection chamber was maintained in an argon (Ar) gas atmosphere to prevent oxidation, and the solution was injected at a temperature of 1450 ° C. to produce the product.
添付した図2乃至図5は、前記各実施例(4〜6)に従って製造された粉末状のFe−Cu合金粒子に対するSEM写真とEDS分析結果を示している。図2は実施例4によるFe−Cu合金粒子の倍率別のSEM写真を示し、図3は実施例4によるFe−Cu合金粒子のEDS分析結果を示し、図4は実施例5によるFe−Cu合金粒子のEDS分析結果を示し、また、図5は実施例6によるFe−Cu合金粒子のEDS分析結果を示している。 Attached FIGS. 2 to 5 show SEM photographs and EDS analysis results for powdered Fe—Cu alloy particles produced according to each of the above Examples (4 to 6). FIG. 2 shows SEM photographs of Fe-Cu alloy particles according to Example 4 by magnification, FIG. 3 shows the results of EDS analysis of Fe-Cu alloy particles according to Example 4, and FIG. 4 shows Fe-Cu according to Example 5. The EDS analysis result of the alloy particles is shown, and FIG. 5 shows the EDS analysis result of the Fe—Cu alloy particles according to Example 6.
図2乃至図5に示したように、各実施例(4〜6)に従って製造されたFe−Cu合金粒子は30mμ以下の微粒子であって、ほとんど完全な球形の形態を有することがわかる。また、図3の下段に示した三つの写真はFeとCuの分布を示しているが(Feは赤色、Cuは緑色)、FeとCuが偏析(偏重)無しに均一に分布していることがわかる。この際、図3の下段に示した三つの写真のうち、真ん中の写真は Feの分布(赤色)を示し、右側の写真はCuの分布(緑色)を示し、また、左側の写真はFeとCuの分布を示している。このように、Fe−Cu合金粒子が完全な球形の形態を有し均一な分布を示すということは、FeとCuが完全な合金をなすということをいう。 As shown in FIGS. 2 to 5, it can be seen that the Fe—Cu alloy particles produced according to each of Examples (4 to 6) are fine particles of 30 μm or less and have an almost perfect spherical morphology. The three photographs shown in the lower part of FIG. 3 show the distribution of Fe and Cu (Fe is red and Cu is green), but Fe and Cu are uniformly distributed without segregation (bias). I understand. At this time, of the three photographs shown in the lower part of FIG. 3, the middle photograph shows the distribution of Fe (red), the photograph on the right shows the distribution of Cu (green), and the photograph on the left shows Fe. The distribution of Cu is shown. As described above, the fact that the Fe—Cu alloy particles have a perfect spherical morphology and show a uniform distribution means that Fe and Cu form a perfect alloy.
一方、添付した図6は比較例2による焼塊(ingot)を用いて噴射させた粒子試片のSEM写真である。図6に示したように、比較例2の場合には、偏析により粒子の形状が不均一な切れ形を示した。これは完全な合金がなされなかったことをいう。
On the other hand, FIG. 6 attached is an SEM photograph of a particle specimen injected by using an ingot according to Comparative Example 2. As shown in FIG. 6, in the case of Comparative Example 2, the particles showed a non-uniform cut shape due to segregation. This means that the perfect alloy was not made.
Claims (8)
(a)熱伝導率 70W/m・K以上、
(b)引張強度 300N/mm2以上、
(c)ブリネル硬度 100HB以上
を呈するように、前記不可避的不純物を除去されていることを特徴とする鉄−銅合金。 An iron-copper alloy containing 5 to 19.5 atomic% of copper and having a component composition in which the balance is Fe and unavoidable impurities.
(A) Thermal conductivity of 70 W / m · K or more,
(B) Tensile strength 300 N / mm 2 or more,
(C) An iron-copper alloy characterized in that the unavoidable impurities have been removed so as to exhibit a Brinell hardness of 100 HB or more.
(a)熱伝導率 70W/m・K以上、
(b)引張強度 300N/mm2以上、
(c)ブリネル硬さ 100HB以上
を呈する鉄−銅合金の製造方法であって、
少なくとも炭素及び酸素を吸収する多孔性の不純物吸収層を内面に与えられた高周波溶解炉に合金原料である鉄及び銅を投入し溶解させ、前記高周波溶解炉の電源を遮断後、1500℃以上で所定時間だけ放置し、インゴットに鋳造することを特徴とする鉄−銅合金の製造方法。 It has a component composition containing 5 to 19.5 atomic% of copper and the balance being Fe and unavoidable impurities.
(A) Thermal conductivity of 70 W / m · K or more,
(B) Tensile strength 300 N / mm 2 or more,
(C) A method for producing an iron-copper alloy having a Brinell hardness of 100 HB or more.
Iron and copper, which are alloy raw materials, are put into a high-frequency melting furnace provided with an inner surface of a porous impurity absorption layer that absorbs at least carbon and oxygen to dissolve them. A method for producing an iron-copper alloy, which comprises leaving it for a predetermined time and casting it into an ingot.
The iron-copper alloy according to any one of claims 4 to 7, wherein the same amount of iron and copper are melted in terms of volume ratio, and then iron is additionally added and melted to give the component composition. Production method.
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