JPS645096B2 - - Google Patents
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- Publication number
- JPS645096B2 JPS645096B2 JP55117192A JP11719280A JPS645096B2 JP S645096 B2 JPS645096 B2 JP S645096B2 JP 55117192 A JP55117192 A JP 55117192A JP 11719280 A JP11719280 A JP 11719280A JP S645096 B2 JPS645096 B2 JP S645096B2
- Authority
- JP
- Japan
- Prior art keywords
- magnetic
- amount
- alloy
- weight
- hardness
- 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.)
- Expired
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- 239000011777 magnesium Substances 0.000 claims description 23
- 229910045601 alloy Inorganic materials 0.000 claims description 14
- 239000000956 alloy Substances 0.000 claims description 14
- 239000010955 niobium Substances 0.000 claims description 9
- 239000010936 titanium Substances 0.000 claims description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 230000035699 permeability Effects 0.000 description 20
- 229910052751 metal Inorganic materials 0.000 description 14
- 239000002184 metal Substances 0.000 description 14
- 230000004907 flux Effects 0.000 description 10
- 238000010586 diagram Methods 0.000 description 7
- 230000007423 decrease Effects 0.000 description 6
- 229910001004 magnetic alloy Inorganic materials 0.000 description 6
- 239000003795 chemical substances by application Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 229910000889 permalloy Inorganic materials 0.000 description 4
- 238000001816 cooling Methods 0.000 description 2
- 230000003009 desulfurizing effect Effects 0.000 description 2
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910044991 metal oxide Inorganic materials 0.000 description 1
- 150000004706 metal oxides Chemical class 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
Landscapes
- Soft Magnetic Materials (AREA)
Description
本発明は、例えば耐摩耗性及び高磁束密度が要
求される磁気ヘツド等に適用して好適なニツケル
―鉄系磁性合金に関し、特にチタン及びニオブの
含有量を規定することにより、他の磁性特性を維
持しながら特に初透磁率及び硬度を更に改善した
磁性合金に関する。
従来、録音再生磁気ヘツド用磁性合金として
は、JIS.PC級パーマロイであるMoパーマロイが
多く用いられている。これは優れた透磁率を有す
る反面、磁性焼鈍後でビツカース硬さHvが120と
低く、従つて磁気テープによる摩耗が著しく寿命
が短かいという欠点がある。磁気ヘツドが摩耗す
ると、磁気記録媒体としてのテープと磁気ヘツド
との密着性が低下してしまい、また磁気ヘツドの
ギヤツプ深さが変化して録音及び再生の特性が著
しく劣化する原因となる。
また磁気ヘツド用磁性合金としては、前述の
Moパーマロイの外に16Al―Fe合金のような高硬
度の材料もあるが、一般的に透磁率が低く、しか
も加工性に劣るという欠点がある。
ところでオーデイオ用磁気テープは、従来、金
属の酸化物が主体であつたが、高性能化が進み、
純鉄を主成分とした新しい素材によるメタルテー
プ（合金テープとも呼ばれる）が開発されてい
る。このメタルテープは高密度記録能力を有する
が、保磁力が約1000エルステツドと大きいため、
従来のヘツド素材では大入力信号でメタルテープ
飽和レベル以前にヘツドの方が先に飽和してしま
うため、音が歪んでしまう問題がある。従つてメ
タルテープの長所である最大出力レベルの改善が
期待できない。
このため従来の飽和磁束密度の低い磁気ヘツド
ではメタルテープの長所が生かされず、メタルテ
ープに対応するためには飽和磁束密度B10が7500
ガウス以上の磁気ヘツドが要求されている。従来
のJIS.PC級パーマロイは、飽和磁束密度が6500
〜7000ガウスと低いため、メタルテープ用録音再
生磁気ヘツド合金としては不適切である。
本発明はかかる点に鑑み、磁気特性に優れ、高
硬度、高磁束密度を有するニツケル―鉄系磁性合
金を提供することを主たる目的とする。
本発明の合金組成は、重量比でNi75〜84.9％、
Ti0.5〜５％、Nb0.3〜0.9％、C0.04％以下及び
Mg0.001〜0.020％を含有し、残部がFe及び不純
物から成る合金において、合金中に残存するＳ量
が0.003％以下としたことを特徴とする。
また脱酸剤として使用されるSi、Al及び脱酸
脱硫剤として使用されるMnが総量で２％以下含
有されることは許される。尚、以下の百分率は重
量％を表わす。
上記各成分のうちNiは75〜84.9％の範囲内では
優れた透磁率を示すが、Niが75％未満では透磁
率が減少し、また84.9％を越えると透磁率及び飽
和磁束密度が減少する
Tiは硬度を上げるために有効であり、0.5％以
上の添加で効何が現われる。Ti量が0.5％未満で
は硬度を上昇させるのが困難である。Ti量が増
加すると硬度も上昇するが、５％を越えると飽和
磁束密度が下がり、透磁率も低下する。
Nbは磁性殊に初透磁率μiの向上に寄与すると
共に、Tiとの相乗効果によりμiを損なうことな
く硬度を著しく向上させ得る。但し、Nbが0.3％
未満ではそれらの効果が少なく、また0.9％を越
えるとTiと共に添加した場合は飽和磁束密度が
低くなるので実用的でない。Nbは規則格子の生
成を抑制し異方性エネルギｋを小さくする効果が
あり、また原子半径がFe、Niに較べて大きいた
めに、Nbを添加した場合固溶体強化現象が現わ
れ硬度が上昇する。
第１表はNbを添加した合金と添加しない合金
の各磁気特性を示している。同表によると、Nb
を添加したものは添加しないものに較べて初透磁
率μi及び硬度が上昇しているのが理解される。
The present invention relates to a nickel-iron magnetic alloy that is suitable for application to, for example, magnetic heads that require wear resistance and high magnetic flux density. The present invention relates to a magnetic alloy that has further improved initial magnetic permeability and hardness while maintaining the following characteristics. Conventionally, Mo permalloy, which is a JIS.PC grade permalloy, has been widely used as a magnetic alloy for recording/reproducing magnetic heads. Although it has excellent magnetic permeability, it has the disadvantage that the Vickers hardness after magnetic annealing is as low as 120 Hv, and therefore the wear caused by the magnetic tape is extremely high and its life is short. When the magnetic head wears out, the adhesion between the magnetic head and the tape as a magnetic recording medium deteriorates, and the gap depth of the magnetic head changes, causing a significant deterioration in recording and playback characteristics. In addition, as magnetic alloys for magnetic heads, the above-mentioned
In addition to Mo permalloy, there are other high-hardness materials such as 16Al-Fe alloys, but they generally have low magnetic permeability and poor workability. By the way, audio magnetic tape has traditionally been made mainly of metal oxides, but with advances in performance,
Metal tape (also called alloy tape) is being developed using a new material whose main component is pure iron. Although this metal tape has high-density recording capability, it has a large coercive force of about 1000 oersteds, so
With conventional head materials, the head becomes saturated before the metal tape saturation level due to large input signals, resulting in sound distortion. Therefore, it cannot be expected to improve the maximum output level, which is an advantage of metal tape. For this reason, conventional magnetic heads with low saturation magnetic flux density cannot take advantage of the advantages of metal tape, and in order to be compatible with metal tape, the saturation magnetic flux density B 10 must be 7500.
A magnetic head of Gauss or higher is required. Conventional JIS.PC grade permalloy has a saturation magnetic flux density of 6500.
Because it is as low as ~7000 Gauss, it is inappropriate as a recording/playback magnetic head alloy for metal tapes. In view of the above, the main object of the present invention is to provide a nickel-iron magnetic alloy having excellent magnetic properties, high hardness, and high magnetic flux density. The alloy composition of the present invention is Ni75 to 84.9% by weight,
Ti0.5~5%, Nb0.3~0.9%, C0.04% or less and
An alloy containing 0.001 to 0.020% Mg and the balance consisting of Fe and impurities, characterized in that the amount of S remaining in the alloy is 0.003% or less. Furthermore, it is permissible for Si and Al used as deoxidizing agents and Mn used as deoxidizing and desulfurizing agents to be contained in a total amount of 2% or less. In addition, the following percentages represent weight %. Among the above components, Ni exhibits excellent magnetic permeability within the range of 75 to 84.9%, but when Ni is less than 75%, the magnetic permeability decreases, and when it exceeds 84.9%, the magnetic permeability and saturation magnetic flux density decrease. Ti is effective for increasing hardness, and its effect becomes apparent when it is added in an amount of 0.5% or more. If the amount of Ti is less than 0.5%, it is difficult to increase the hardness. As the amount of Ti increases, the hardness also increases, but when it exceeds 5%, the saturation magnetic flux density decreases and the magnetic permeability also decreases. Nb contributes to improving magnetism, particularly initial permeability μi, and can significantly improve hardness without impairing μi due to its synergistic effect with Ti. However, Nb is 0.3%
If it is less than 0.9%, these effects will be small, and if it exceeds 0.9%, the saturation magnetic flux density will be low when added together with Ti, which is not practical. Nb has the effect of suppressing the formation of a regular lattice and reducing the anisotropic energy k, and also has a larger atomic radius than Fe and Ni, so when Nb is added, a solid solution strengthening phenomenon occurs and the hardness increases. Table 1 shows the magnetic properties of alloys with and without Nb added. According to the same table, Nb
It is understood that the initial magnetic permeability μi and hardness of the steel with which .
【表】
第１図は炭素Ｃの添加量と初透磁率μiとの関係
を示す特性曲線図である。Ｃは脱酸剤として添加
するものであるが、Ｃ含有量が増加するに従い初
透磁率μiは減少していく。Ｃ量が0.03％以上では
初透磁率が低く実用に供し得ない。
Mgは本合金の熱間加工性を改善するために脱
硫剤として添加するものであり、脱酸を充分に行
なつてから添加する必要がある。脱酸としてはＣ
脱酸が磁気特性向上の点から最も効果的である。
第２図は本発明合金の試験温度と引張試験におけ
る断面収縮率との関係を示す線図である。同図に
示す如く、Mgを添加したものはMg無添加のも
のに較べて断面収縮率が大きくなつている。断面
収縮率が大きい程熱間加工性は良好となる。この
ことからMgを添加することにより熱間加工性が
著しく改善されることがわかる。第３図はMg量
と初透磁率μi及び断面収縮率（試験温度1200℃）
との関係を示す。同図に示す如く、初透磁率μiは
Mg量が増加すると共に低下し、Mg量が0.02％を
越えるとμiが低くなるため、実用に供し得ない。
また断面収縮率はMg量が増加すると共に大きく
なり、Mg量が0.02％で飽和値を示している。以
上のことからMgを添加することにより熱間加工
性は著しく改善され、Mg量が0.001％未満では熱
間加工性の改善効果が少なく、0.020％を越える
と熱間加工性の改善に寄与しないのみならず、磁
気特性殊に初透磁率μiを低下させるためにMg量
は0.001〜0.020％の範囲が有効である。
次に本発明合金の製法の一例について説明する
に、第１表に示す組成の各インゴツトをNi、Fe、
Tiの適当量を真空中において適当な溶解炉を用
いて溶解し組成的に均一な溶湯を作り、これにま
ず脱酸剤としてＣを適当量添加し充分脱酸を行な
つた後、溶湯中のＳ量の10〜30倍のMgを添加し
脱硫するのが最も効果的である。このMgによる
脱硫はMgSを形成せしめることが目的であるた
め、溶湯中のＳ量とほぼ同量のMgを添加すれば
充分であるが、Mgは融点が654℃と低いために
添加量の１／10程度しか溶湯中に残らず殆ど蒸発
してしまうため上記の通り溶湯中のＳ量の10〜30
倍のMgを添加する必要がある。これ得られた溶
湯を適当な鋳型に注入して健全なインゴツトを製
造し、通常の熱間加工、冷間加工を施し、板厚
0.099mmまで圧延した。熱間加工においては、耳
われ、クラツク等が生ぜず、熱間加工性が良好で
あつた。そしてその板材より外径10mm内径６mmの
リングを打抜き試料とした。これらの試料を水素
雰囲気中にて1100℃で３時間保持した後、200
℃／Hrの冷却速度で冷却した。このようにして
得られた各試料の飽和磁束密度B10、保磁力Hc、
初透磁率μi及び硬さHvを測定した結果を前記第
１表に示す。
尚、含有Ｓ量を分析した結果、いずれの試料に
おいてもＳ量は0.003％以下であつた。
次に、合金中のMgの存在形態を調査するため
にＸ線マイクロアナライザによる線分析を行つ
た。この結果を第４図に示す。第４図よりMg―
KαとＳ―Kαが極大となる位置は一致しており、
またＯ―Kαは殆ど変動が認められないことから
MgSが形成されていることが確認された。
以上述べた如く本発明によれば、ニツケル75〜
84.9重量％、チタン0.5〜５重量％、ニオブ0.3〜
0.9重量％、炭素0.03重量％以下（零を含まず）
及びマグネシウム0.001〜0.0020重量％含有し、
残部が鉄及び不純物から成る磁性合金において、
該合金中に残存する硫黄の量が0.003重量％以下
と構成したので、チタン及びニオブの相乗効果に
より初透磁率を損なうことなく硬度を著しく向上
させることができる。すなわち、熱間加工性に優
れ、Hv＝150以上の硬度を有しながらも、飽和磁
束密度が高く磁気特性に優れている効果を有す
る。従つて本発明合金をメタルテープ用録音再生
磁気ヘツドに適用することにより、録音再生特性
が向上する。また電子計算機、VTR等の高速摺
動用磁気ヘツドに適用すると好適である。[Table] FIG. 1 is a characteristic curve diagram showing the relationship between the amount of carbon C added and the initial magnetic permeability μi. C is added as a deoxidizing agent, and as the C content increases, the initial magnetic permeability μi decreases. If the C content is 0.03% or more, the initial magnetic permeability will be low and it cannot be put to practical use. Mg is added as a desulfurizing agent to improve the hot workability of this alloy, and must be added after sufficient deoxidation. C as a deoxidizer
Deoxidation is most effective in terms of improving magnetic properties.
FIG. 2 is a diagram showing the relationship between test temperature and cross-sectional shrinkage rate in a tensile test for the alloy of the present invention. As shown in the figure, the cross-sectional shrinkage ratio of the material with Mg added is greater than that of the material without Mg. The larger the cross-sectional shrinkage rate, the better the hot workability. This shows that hot workability is significantly improved by adding Mg. Figure 3 shows Mg content, initial permeability μi, and cross-sectional shrinkage rate (test temperature 1200℃)
Indicates the relationship between As shown in the figure, the initial magnetic permeability μi is
It decreases as the Mg amount increases, and when the Mg amount exceeds 0.02%, μi becomes low and cannot be put to practical use.
Further, the cross-sectional shrinkage ratio increases as the Mg content increases, and reaches a saturation value at a Mg content of 0.02%. From the above, hot workability is significantly improved by adding Mg, and if the amount of Mg is less than 0.001%, the effect of improving hot workability is small, and if it exceeds 0.020%, it does not contribute to improvement of hot workability. In addition, in order to reduce the magnetic properties, particularly the initial magnetic permeability μi, it is effective to set the Mg amount in the range of 0.001 to 0.020%. Next, to explain an example of the method for manufacturing the alloy of the present invention, each ingot having the composition shown in Table 1 is
An appropriate amount of Ti is melted in a vacuum using an appropriate melting furnace to create a compositionally uniform molten metal.First, an appropriate amount of C is added as a deoxidizing agent to sufficiently deoxidize, and then the molten metal is It is most effective to desulfurize by adding Mg in an amount 10 to 30 times the amount of S. Since the purpose of desulfurization using Mg is to form MgS, it is sufficient to add almost the same amount of Mg as the amount of S in the molten metal, but since Mg has a low melting point of 654°C, As mentioned above, only about 10 to 30 of the S amount in the molten metal remains in the molten metal and most of it evaporates.
It is necessary to add twice as much Mg. The resulting molten metal is poured into a suitable mold to produce a sound ingot, which is then subjected to normal hot working and cold working to reduce the plate thickness.
It was rolled to 0.099mm. In hot working, no cracks or cracks were produced, and the hot workability was good. A ring with an outer diameter of 10 mm and an inner diameter of 6 mm was punched out from the plate and used as a sample. After holding these samples at 1100℃ for 3 hours in a hydrogen atmosphere,
Cooling was performed at a cooling rate of °C/Hr. Saturation magnetic flux density B 10 , coercive force Hc of each sample obtained in this way,
The results of measuring the initial magnetic permeability μi and hardness Hv are shown in Table 1 above. As a result of analyzing the S content, the S content was 0.003% or less in all samples. Next, in order to investigate the existence form of Mg in the alloy, line analysis was performed using an X-ray microanalyzer. The results are shown in FIG. From Figure 4, Mg―
The positions where Kα and S−Kα are maximum are the same,
In addition, since almost no fluctuation is observed in O-Kα,
It was confirmed that MgS was formed. As described above, according to the present invention, Nickel 75~
84.9% by weight, titanium 0.5~5% by weight, niobium 0.3~
0.9% by weight, carbon 0.03% by weight or less (not including zero)
and magnesium 0.001 to 0.0020% by weight,
In a magnetic alloy where the remainder is iron and impurities,
Since the amount of sulfur remaining in the alloy is 0.003% by weight or less, the synergistic effect of titanium and niobium can significantly improve the hardness without impairing the initial magnetic permeability. That is, it has excellent hot workability, has a hardness of Hv=150 or more, and has a high saturation magnetic flux density and excellent magnetic properties. Therefore, by applying the alloy of the present invention to a recording/reproducing magnetic head for metal tape, the recording/reproducing characteristics are improved. It is also suitable for application to high-speed sliding magnetic heads for computers, VTRs, etc.
第１図は炭素添加量と初透磁率μiとの関係を示
す線図、第２図は本発明合金の試験温度と引張試
験における断面収縮率との関係を示す線図、第３
図はマグネシウム量と初透磁率μi及び断面収縮率
との関係を示す線図、第４図はMgの存在形態の
説明に供する線図である。
Fig. 1 is a diagram showing the relationship between the amount of carbon added and the initial magnetic permeability μi, Fig. 2 is a diagram showing the relationship between the test temperature of the alloy of the present invention and the cross-sectional shrinkage rate in a tensile test, and Fig. 3 is a diagram showing the relationship between the amount of carbon added and the initial magnetic permeability μi.
The figure is a diagram showing the relationship between the amount of magnesium, the initial magnetic permeability μi, and the cross-sectional shrinkage rate, and FIG. 4 is a diagram used to explain the existence form of Mg.
Claims (1)
量％、ニオブ0.3〜0.9重量％、炭素0.03重量％以
下（零を含まず）及びマグネシウム0.001〜0.020
重量％含有し、残部が鉄及び不純物から成る合金
であつて、該合金中に残存するＳ量が0.003重量
％以下としたことを特徴とする磁性合金。1 Nickel 75-84.9% by weight, titanium 0.5-5% by weight, niobium 0.3-0.9% by weight, carbon 0.03% by weight or less (not including zero), and magnesium 0.001-0.020
% by weight, the remainder consisting of iron and impurities, characterized in that the amount of S remaining in the alloy is 0.003% by weight or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55117192A JPS5741341A (en) | 1980-08-25 | 1980-08-25 | Magnetic alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55117192A JPS5741341A (en) | 1980-08-25 | 1980-08-25 | Magnetic alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5741341A JPS5741341A (en) | 1982-03-08 |
| JPS645096B2 true JPS645096B2 (en) | 1989-01-27 |
Family
ID=14705675
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP55117192A Granted JPS5741341A (en) | 1980-08-25 | 1980-08-25 | Magnetic alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5741341A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2521722Y2 (en) * | 1989-04-20 | 1997-01-08 | 大日本印刷株式会社 | Easy-open packaging |
-
1980
- 1980-08-25 JP JP55117192A patent/JPS5741341A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5741341A (en) | 1982-03-08 |
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