JPH01191754A - Manufacture of nitride grain-containing amorphous alloy - Google Patents
Manufacture of nitride grain-containing amorphous alloyInfo
- Publication number
- JPH01191754A JPH01191754A JP1423988A JP1423988A JPH01191754A JP H01191754 A JPH01191754 A JP H01191754A JP 1423988 A JP1423988 A JP 1423988A JP 1423988 A JP1423988 A JP 1423988A JP H01191754 A JPH01191754 A JP H01191754A
- Authority
- JP
- Japan
- Prior art keywords
- nitride
- alloy
- amorphous
- atom
- denotes
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 150000004767 nitrides Chemical class 0.000 title claims abstract description 39
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 239000000956 alloy Substances 0.000 claims abstract description 31
- 229910052751 metal Inorganic materials 0.000 claims abstract description 19
- 238000010791 quenching Methods 0.000 claims abstract description 10
- 230000000171 quenching effect Effects 0.000 claims abstract description 10
- 238000002844 melting Methods 0.000 claims abstract description 9
- 230000008018 melting Effects 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 229910052763 palladium Inorganic materials 0.000 claims abstract description 3
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 2
- 229910052742 iron Inorganic materials 0.000 claims abstract 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 34
- 239000002245 particle Substances 0.000 claims description 20
- 239000002184 metal Substances 0.000 claims description 17
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- 238000000034 method Methods 0.000 claims description 15
- 239000007788 liquid Substances 0.000 claims description 11
- 239000007789 gas Substances 0.000 claims description 8
- 229910045601 alloy Inorganic materials 0.000 abstract description 23
- 239000011159 matrix material Substances 0.000 abstract description 14
- 238000001816 cooling Methods 0.000 abstract description 5
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000463 material Substances 0.000 description 20
- 239000000843 powder Substances 0.000 description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- 239000010949 copper Substances 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 229910052786 argon Inorganic materials 0.000 description 3
- 239000011162 core material Substances 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 230000035699 permeability Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 229910000669 Chrome steel Inorganic materials 0.000 description 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000009987 spinning Methods 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
Landscapes
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
Description
【発明の詳細な説明】
「技術分野」
本発明は、非晶質は相中に窒化物粒子を含有させた窒化
物粒子含有非晶質合金の製造法に関する。DETAILED DESCRIPTION OF THE INVENTION [Technical Field] The present invention relates to a method for producing an amorphous alloy containing nitride particles, in which the amorphous phase contains nitride particles.
「従来技術およびその問題点」
従来、金属溶湯に窒化物や炭化物の粉末を強制的に添加
し急冷することによって、非晶質母相中に窒化物や炭化
物粒子を分散させた合金が得られることが知られている
。このような非晶質合金は、硬度が高＜、耐腐食性に優
れるという非晶質合金の特性を備えると共に１分散した
窒化物や炭化物によって硬度や耐摩耗性などの材料特性
がさらに向上する。"Prior art and its problems" Conventionally, by forcibly adding nitride or carbide powder to molten metal and rapidly cooling it, an alloy with nitride or carbide particles dispersed in an amorphous matrix can be obtained. It is known. Such amorphous alloys have the characteristics of amorphous alloys such as high hardness and excellent corrosion resistance, and the material properties such as hardness and wear resistance are further improved by dispersed nitrides and carbides. .
しかしながら、上記のような製造方法では、金属溶湯中
に窒化物や炭化物の粉末を添加する際、溶湯との濡れ性
の悪いことや、比重の違い等によって粉末を均一に分散
させることが困難であった。また、窒化物などの粉末は
、高価であるという問題点もあった。However, with the above manufacturing method, when adding nitride or carbide powder to molten metal, it is difficult to uniformly disperse the powder due to poor wettability with the molten metal and differences in specific gravity. there were. Another problem is that powders such as nitrides are expensive.
「発明の目的Ｊ
本発明の目的は、非晶質合金からなる母相中にプラズマ
アーク反応によって生成された窒化物の微細な粒子を均
一に分散させることにより、強度、硬度、磁気特性など
に優れた効果を有する窒化物粒子含有非晶質合金の製造
法を提供することにある。"Objective of the Invention J The object of the present invention is to improve strength, hardness, magnetic properties, etc. by uniformly dispersing fine nitride particles generated by plasma arc reaction in a matrix consisting of an amorphous alloy. An object of the present invention is to provide a method for producing an amorphous alloy containing nitride particles that has excellent effects.
「発明の構成」
本発明による窒化物粒子含有非晶質合金の製造法は、窒
化物形成可能な元素を含有する非晶質合金材料を窒素あ
るいは窒素を含む混合ガス中でプラズマアークにより溶
解し、その溶湯を液体急冷法で急冷凝固することにより
、非晶質母相中に窒化物が均一分散した合金を得ること
を特徴とする。"Structure of the Invention" The method for producing an amorphous alloy containing nitride particles according to the present invention involves melting an amorphous alloy material containing an element capable of forming nitrides by plasma arc in nitrogen or a mixed gas containing nitrogen. The molten metal is rapidly solidified using a liquid quenching method to obtain an alloy in which nitrides are uniformly dispersed in an amorphous matrix.
このように、窒化物形成可能な元素を含有する非晶質合
金材料を窒素ガス中でアーク溶解したとき、プラズマ中
で活性化された窒素と溶融金属との反応により窒化物を
生成し、この溶湯を液体急冷することにより非晶質の組
織が形成されると共に、窒化物を均一に分散した合金を
得ることができる。In this way, when an amorphous alloy material containing an element capable of forming nitrides is arc melted in nitrogen gas, nitrides are generated by the reaction between the nitrogen activated in the plasma and the molten metal. By rapidly liquid cooling the molten metal, an amorphous structure is formed and an alloy in which nitrides are uniformly dispersed can be obtained.
そして、この合金は、窒化物からなる粒径的０．５〜５
μｍの微細な粒子が均一に分散していることから、強度
および硬度が向上し、磁気特性、特に高周波領域の向上
が図られ、結晶化温度も高くなるなど、優れた性質を有
しており、薄帯、細線、圧粉体などとして、例えば磁気
ヘッド、高周波用巻鉄心などの電子部品材料、高強度部
品材料、耐摩耗性材料などとして好適なものである。This alloy consists of nitrides with a grain size of 0.5 to 5.
Because micron-sized particles are uniformly dispersed, it has excellent properties such as improved strength and hardness, improved magnetic properties, especially in the high frequency range, and a higher crystallization temperature. It is suitable as a thin ribbon, a fine wire, a powder compact, etc., for example, as a material for electronic parts such as magnetic heads and high-frequency wound cores, a material for high-strength parts, and a wear-resistant material.
本発明において、窒化物形成可能な元素を含有する非晶
質合金材料としては、窒化物を形成する元素を有し、液
体急冷凝固したときに非晶質となる合金組成でなければ
ならない、この場合、窒化物形成元素としては、Ｖ、Ｃ
ｒ、Ｚｒ、Ｔｉ、Ｔａ、Ｎｂ、Ｈｆ、Ｍｏ、Ｗ、ＡＩか
ら選ばれた一＋ｉまたは二種以上が用いられる。In the present invention, the amorphous alloy material containing an element that can form a nitride must have an alloy composition that contains an element that forms a nitride and becomes amorphous when solidified by rapid liquid cooling. In this case, the nitride-forming elements include V, C
One+i or two or more selected from r, Zr, Ti, Ta, Nb, Hf, Mo, W, and AI are used.
上記のような非晶質合金材料としては、−８式％式％
Ｃｏ、Ｎｉ、Ｃｕ、Ｐｄからなる群より選ばれたー神ま
たは二種以上の元素、βはＢ、Ｓｉ、“Ｐ、Ｇｅからな
る群より選ばれた一種または二種以上の元素、Ｃは炭素
１Ｍは窒化物形成元素であるＶ、Ｃｒ、Ｚｒ、Ｔｉ、Ｔ
ａ、Ｎｂ、Ｈｆ。The above-mentioned amorphous alloy materials include -8 formula % formula % - element or two or more elements selected from the group consisting of Co, Ni, Cu, Pd, β is B, Si, "P, One or more elements selected from the group consisting of Ge, C is carbon 1M is a nitride forming element V, Cr, Zr, Ti, T
a, Nb, Hf.
Ｍｏ、Ｗ、ＡＩから選ばれた一種または二種以上の元素
を表わし、ＸはｌＯ〜３５原子％、ｙは２〜１５原子％
、Ｚは２〜２５原子％であり、かつｘ＋ｙは１２〜４０
原子％である。）で示される合金材料が使用できる。こ
こで、α、βは非晶質の母相を形成する元素であり、Ｃ
，Ｍは窒化物形成の際必要な元素である。上記一般式に
おいて、Ｘが１０未満あるいはＸが３５を超えると、元
素α、βによって非晶質な母相を形成することが困難と
なる。また、ｙが２未満では、窒化物の形成が困難とな
り、ｙが１５を超えると窒化物粒子が大きくなり、脆く
なる傾向がある。また、Ｚが２未満では窒化物形成が困
難となり、Ｚが２５を超えると、非晶質母相形成が困難
となる。なお、Ｘとｙとの加算量が１２未満あるいは４
０以上では、非晶質母相形成が困難となる。Represents one or more elements selected from Mo, W, and AI, where X is lO to 35 at% and y is 2 to 15 at%.
, Z is 2 to 25 atom%, and x+y is 12 to 40
It is atomic percent. ) can be used. Here, α and β are elements that form an amorphous matrix, and C
, M are elements necessary for nitride formation. In the above general formula, when X is less than 10 or exceeds 35, it becomes difficult to form an amorphous matrix due to the elements α and β. Furthermore, when y is less than 2, it becomes difficult to form nitrides, and when y exceeds 15, nitride particles tend to become large and brittle. Further, when Z is less than 2, it becomes difficult to form a nitride, and when Z exceeds 25, it becomes difficult to form an amorphous matrix. In addition, if the addition amount of X and y is less than 12 or 4
If it is 0 or more, it becomes difficult to form an amorphous matrix.
本発明では、まず、上記の合金を窒素あるいは窒素を含
む混合ガス雰囲気中でアーク溶解する。In the present invention, first, the above alloy is arc melted in an atmosphere of nitrogen or a mixed gas containing nitrogen.
ここで、窒素を含む混合ガスとしては、例えば窒素＋ア
ルゴン、窒素十水素、窒素＋ヘリウムなどの混合ガスが
使用される。また、アーク溶解は。Here, as the mixed gas containing nitrogen, a mixed gas such as nitrogen + argon, nitrogen dehydrogen, nitrogen + helium, etc. is used. Also, arc melting.
例えば水冷銅ハース上の試料（陽極）とタングステン電
極（陰極）の間でアークを発生させ、試料を溶解するこ
とによりなされる。このアーク溶解により、窒素プラズ
マ−金属間の反応が起こり、溶湯中に微細な窒化物が生
成する。生成する窒化物粒子の量および寸法は、主にア
ーク溶解時の窒素分圧および合金中の窒化物形成元素Ｍ
の種類と量に強く依存する。For example, this is done by generating an arc between a sample (anode) on a water-cooled copper hearth and a tungsten electrode (cathode) to melt the sample. This arc melting causes a reaction between the nitrogen plasma and the metal, producing fine nitrides in the molten metal. The amount and size of the nitride particles produced are mainly determined by the nitrogen partial pressure during arc melting and the nitride-forming element M in the alloy.
strongly depends on the type and amount of
次に、上記溶湯を液体急冷法により急冷凝固させる。こ
の液体急冷法とは、溶融した金属、合金を急速に冷却し
て適冷させ、その構造を凍結させて非晶質（アモルファ
ス）とする方法をいい、例えば薄帯材料を得るには、単
ロール法、双ロール法、ハンマーアンビル法などが特に
有効であり、これらの方法は１０’〜１０’℃／秒の冷
却速度を有している。この単ロール法、双ロール法など
により薄帯材料を製造するには、上記合金の溶湯を、液
体状態の温度より、ノズル孔を通して、約３００〜ｌｏ
ｏｏｏｒｐｍで回転している直径３０〜３０００ｍｍの
銅あるいはクロム鋼製などの金属製ロール上に溶湯を噴
出すればよく、これにより、幅約１〜２００ｍｍで、厚
さが約５〜２００μｍの薄帯材料を容易に得ることがで
きる。また、ハンマーアンビル法で薄板材料を製造する
には、水冷銅ハース上で溶融した溶湯を銅製のハンマー
で叩くことにより得ることができる。Next, the molten metal is rapidly solidified by a liquid quenching method. This liquid quenching method refers to a method in which a molten metal or alloy is rapidly cooled and cooled appropriately, and its structure is frozen to become amorphous. For example, to obtain a thin strip material, a single Particularly effective are the roll method, twin roll method, hammer anvil method, etc., and these methods have a cooling rate of 10' to 10'C/sec. To produce a ribbon material by this single roll method, twin roll method, etc., the molten metal of the above alloy is heated from a liquid state temperature through a nozzle hole to a
The molten metal may be spouted onto a metal roll made of copper or chrome steel with a diameter of 30 to 3000 mm rotating at ooorpm, thereby forming a thin strip with a width of approximately 1 to 200 mm and a thickness of approximately 5 to 200 μm. Materials can be easily obtained. Further, in order to produce a thin plate material by the hammer anvil method, it can be obtained by hitting molten metal melted on a water-cooled copper hearth with a copper hammer.
このように、プラズマアーク溶解後の溶湯状態から液体
急冷法により急冷凝固させると、例えば母相中に１粒径
が０．５〜５μｍ程度の非常に微細な窒化物粒子が、１
〜４μｍ程度の間隔で均一に分散した組織となり、前述
したような優れた特性を有する窒化物粒子含有非晶質合
金が得られる。また、上記工程において、プラズマアー
ク溶解後、−旦凝固させた合金を原料として液体急冷法
に供しても同様な特徴を有する合金が得られる。さらに
１本発明の合金は、例えば回転水中紡糸法による線材、
ガス噴霧法や回転板法などによる粉体としても得ること
ができる。In this way, when the molten metal after plasma arc melting is rapidly solidified by the liquid quenching method, very fine nitride particles with a grain size of about 0.5 to 5 μm are formed in the matrix, for example.
A uniformly dispersed structure is obtained at intervals of about 4 μm, and an amorphous alloy containing nitride particles having excellent properties as described above is obtained. Moreover, in the above process, an alloy having similar characteristics can be obtained by subjecting the solidified alloy to a liquid quenching method as a raw material after plasma arc melting. Furthermore, the alloy of the present invention can be used, for example, as a wire rod produced by a rotating underwater spinning method.
It can also be obtained as a powder by a gas atomization method or a rotating plate method.
「発明の実施例」
実施例１〜４、比較例１
第１表に示す各種組成よりなる合金を、窒素十アルゴン
（１： ｌ）混合ガス雰囲気中でプラズマアークにより
溶解し、プラズマ中で活性化された窒素と溶融金属とを
反応せしめた後、ハンマーアンビル法で液体急冷するこ
とにより、直径４０ｍｍ、厚さ１００μｍの薄板材料を
得た。こうして得られた各薄板材料の結晶化温度Ｔｘ
（Ｋ）、ビッカース硬度）１ｖ （ＤＰＮ）、引張強さ
（Ｋｇｆ／ｍｍ”）を測定した。この結果を第１表に示
す。"Embodiments of the Invention" Examples 1 to 4, Comparative Example 1 Alloys having various compositions shown in Table 1 were melted by a plasma arc in a nitrogen/ten argon (1: l) mixed gas atmosphere, and activated in the plasma. A thin plate material having a diameter of 40 mm and a thickness of 100 μm was obtained by reacting the molten metal with the molten nitrogen and then liquid quenching using a hammer anvil method. Crystallization temperature Tx of each thin plate material thus obtained
(K), Vickers hardness) 1v (DPN), and tensile strength (Kgf/mm"). The results are shown in Table 1.
第１表から、非晶質の母相中にＺｒＮ、ＮｂＮなどの窒
化物粒子を分散させた実施例１〜４の薄板材料は、非晶
質母相のみからなる比較例１の薄板材料に比べて、結晶
化温度Ｔｘが高くなり、ビッカース硬度も向上している
ことがわかる。From Table 1, it can be seen that the thin plate materials of Examples 1 to 4 in which nitride particles such as ZrN and NbN are dispersed in an amorphous matrix are different from the thin plate material of Comparative Example 1 consisting only of an amorphous matrix. In comparison, it can be seen that the crystallization temperature Tx is higher and the Vickers hardness is also improved.
実施例１および実施例３で得られた薄板のＣｕ−Ｋａｌ
ｌによるＸ線回折チャートを第１図に示す、第１図中、
・はＮｂＮの位置を示し、マはＺｒＮの位置を示してい
る。この結果より、実施例１で得られた薄板は非晶質＋
Ｎｂ （Ｃ，Ｎ）。Cu-Kal thin plates obtained in Example 1 and Example 3
Figure 1 shows an X-ray diffraction chart according to l, in Figure 1,
* indicates the position of NbN, and ma indicates the position of ZrN. From this result, the thin plate obtained in Example 1 is amorphous +
Nb(C,N).
実施例３で得られた薄板は非晶質＋Ｚｒ （Ｃ。The thin plate obtained in Example 3 was amorphous + Zr (C.
Ｎ）の組織になっていることがわかる。It can be seen that the organization is N).
また、第２図に実施例１で得られた薄板材料の断面の光
学顕微鏡組織写真を示す、この写真から非晶質の母相中
に、粒径が約０．５〜３μｍの非常に微細な窒化物粒子
が、およそ２〜４μｍの間隔で均一に分散した組織を有
していることが確認された。In addition, Fig. 2 shows an optical microscopic structure photograph of the cross section of the thin plate material obtained in Example 1. From this photograph, it can be seen that there are very fine grains with a diameter of about 0.5 to 3 μm in the amorphous matrix. It was confirmed that the nitride particles had a structure in which they were uniformly dispersed at intervals of approximately 2 to 4 μm.
実施例５、比較例１
第２表に示す組成よりなる合金を、窒素＋アルボン（１
： ｌ）混合ガス雰囲気中でプラズマアークにより溶解
した後、凝固させた母材を原料として、単ロール法で液
体急冷することにより１幅約３ｍｍ、厚さ約１５μｍの
薄帯材料を得た。こうして得られた薄帯材料をキュリ温
度以上５０にで１０分焼きなましした後、空冷した試料
の実効透磁率（０，０１０ｅ６ａ場）を測定した。第２
表に見るように、実施例５で得られた薄帯は、飽和磁化
は若干低（なるが、高周波領域における透磁率の低下が
比較例２に比べて非常に小さく、高周波用鉄心材料とし
て好ましい特性を有していることが確認された。Example 5, Comparative Example 1 An alloy having the composition shown in Table 2 was mixed with nitrogen + arbon (1
: l) A thin strip material having a width of about 3 mm and a thickness of about 15 μm was obtained by liquid quenching using a single roll method using the solidified base material as a raw material after being melted by a plasma arc in a mixed gas atmosphere. The ribbon material thus obtained was annealed for 10 minutes at 50°C above the Curie temperature, and then the effective magnetic permeability (0,010e6a field) of the air-cooled sample was measured. Second
As seen in the table, the saturation magnetization of the ribbon obtained in Example 5 is slightly low (although the decrease in magnetic permeability in the high frequency region is very small compared to Comparative Example 2), making it preferable as a high frequency iron core material. It was confirmed that it has the following characteristics.
（以下、余白）
実施例６〜１０
第３表に示す組成よりなる合金を、窒素ガス雰囲気中で
プラズマアークにより溶解したインゴットを用いて、ア
ルゴンガス噴霧装置により液体急冷して、約１０〜８０
μｍ径の粒状粉末材料を得た。こうして得られた粉末の
Ｘ線回折組織、光学顕微鏡による粒子形態を調べた。第
３表に見るように、実施例６〜１０の各試料は、いずれ
も非晶質母相と窒化物粒子からなり、粒子は０．１〜５
μｍ径で、１〜４μｍの間隔で均一に分散しているのが
確認された。(Hereinafter, blank space) Examples 6 to 10 Using an ingot melted by a plasma arc in a nitrogen gas atmosphere, an alloy having the composition shown in Table 3 was quenched with an argon gas atomizer, and the alloy was melted to about 10 to 80%
A granular powder material with a diameter of μm was obtained. The powder thus obtained was examined for its X-ray diffraction structure and particle morphology using an optical microscope. As shown in Table 3, each sample of Examples 6 to 10 consists of an amorphous matrix and nitride particles, and the particles are 0.1 to 5
It was confirmed that the particles were uniformly dispersed at intervals of 1 to 4 μm in diameter.
（以下、余白）
「発明の効果」
以上説明したように１本発明によれば、非晶質の母相中
に１粒径約０．５〜５μｍの微細な窒化物粒子が均一に
分散した合金を得ることができ、この合金は、強度およ
び硬度が向上し、磁気特性、特に高周波領域の向上が図
られ、結晶化温度も高くなるなど、優れた性質を有して
おり、例えば電磁材料、強度材料、耐摩耗材料などとし
て好適なものである。(Hereinafter, blank space) "Effects of the Invention" As explained above, according to the present invention, fine nitride particles each having a diameter of about 0.5 to 5 μm are uniformly dispersed in the amorphous matrix. This alloy has excellent properties such as improved strength and hardness, improved magnetic properties, especially in the high frequency range, and a higher crystallization temperature. For example, it can be used as an electromagnetic material. It is suitable as a strength material, a wear-resistant material, etc.
第１図は本発明の実施例１．３で得られた合金のＸ線回
折チャート、第２図は本発明の実施例１で得られた合金
の断面を示す光学顕微鏡組織写真である。FIG. 1 is an X-ray diffraction chart of the alloy obtained in Example 1.3 of the present invention, and FIG. 2 is an optical micrograph showing the cross section of the alloy obtained in Example 1 of the present invention.
Claims (2)
を窒素あるいは窒素を含む混合ガス中でプラズマアーク
により溶解し、その溶湯を液体急冷法で急冷凝固させる
ことを特徴とする窒化物粒子含有非晶質合金の製造法。(1) A nitride is produced by melting an amorphous alloy material containing an element capable of forming a nitride using a plasma arc in nitrogen or a mixed gas containing nitrogen, and rapidly solidifying the molten metal using a liquid quenching method. Method for producing particle-containing amorphous alloy.
可能な元素を含有する非晶質合金材料として、α＿１＿
０＿０＿−＿ｘ＿−＿ｙ＿−＿ｚβ＿ｘＣ＿ｙＭ＿ｚ（
ここで、αはＦｅ、Ｃｏ、Ｎｉ、Ｃｕ、Ｐｄからなる群
より選ばれた一種または二種以上の元素、βはＢ、Ｓｉ
、Ｐ、Ｇｅからなる群より選ばれた一種または二種以上
の元素、Ｃは炭素、Ｍは窒化物形成元素であるＶ、Ｃｒ
、Ｚｒ、Ｔｉ、Ｔａ、Ｎｂ、Ｈｆ、Ｍｏ、Ｗ、Ａｌから
選ばれた一種または二種以上の元素を表わし、ｘは１０
〜３５原子％、ｙは２〜１５原子％、ｚは２〜２５原子
％であり、かつｘ＋ｙは１２〜４０原子％である。）で
示される合金材料を使用する窒化物粒子含有非晶質合金
の製造法。(2) In claim 1, the amorphous alloy material containing the nitride-forming element is α_1_
0_0_-_x_-_y_-_zβ_xC_yM_z(
Here, α is one or more elements selected from the group consisting of Fe, Co, Ni, Cu, and Pd, β is B, Si
, P, one or more elements selected from the group consisting of Ge, C is carbon, and M is a nitride-forming element V, Cr
, Zr, Ti, Ta, Nb, Hf, Mo, W, and Al, and x represents 10
~35 atom %, y is 2 to 15 atom %, z is 2 to 25 atom %, and x+y is 12 to 40 atom %. ) A method for producing an amorphous alloy containing nitride particles using the alloy material shown in
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1423988A JPH01191754A (en) | 1988-01-25 | 1988-01-25 | Manufacture of nitride grain-containing amorphous alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1423988A JPH01191754A (en) | 1988-01-25 | 1988-01-25 | Manufacture of nitride grain-containing amorphous alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01191754A true JPH01191754A (en) | 1989-08-01 |
Family
ID=11855533
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1423988A Pending JPH01191754A (en) | 1988-01-25 | 1988-01-25 | Manufacture of nitride grain-containing amorphous alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01191754A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5884936A (en) * | 1981-11-13 | 1983-05-21 | Nissan Motor Co Ltd | Manufacture of heat resistant aluminum alloy |
| JPS6017029A (en) * | 1983-07-09 | 1985-01-28 | Alps Electric Co Ltd | Production of second phase particle dispersion type ultraquickly cooled alloy |
| JPS6017028A (en) * | 1983-07-09 | 1985-01-28 | Alps Electric Co Ltd | Production of second phase particle dispersion type ultraquickly cooled alloy |
-
1988
- 1988-01-25 JP JP1423988A patent/JPH01191754A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5884936A (en) * | 1981-11-13 | 1983-05-21 | Nissan Motor Co Ltd | Manufacture of heat resistant aluminum alloy |
| JPS6017029A (en) * | 1983-07-09 | 1985-01-28 | Alps Electric Co Ltd | Production of second phase particle dispersion type ultraquickly cooled alloy |
| JPS6017028A (en) * | 1983-07-09 | 1985-01-28 | Alps Electric Co Ltd | Production of second phase particle dispersion type ultraquickly cooled alloy |
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