JPS62124264A - Manufacture of ni-fe alloy - Google Patents
Manufacture of ni-fe alloyInfo
- Publication number
- JPS62124264A JPS62124264A JP26239085A JP26239085A JPS62124264A JP S62124264 A JPS62124264 A JP S62124264A JP 26239085 A JP26239085 A JP 26239085A JP 26239085 A JP26239085 A JP 26239085A JP S62124264 A JPS62124264 A JP S62124264A
- Authority
- JP
- Japan
- Prior art keywords
- temp
- alloy
- mold
- billet
- heat treatment
- 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.)
- Granted
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 229910000640 Fe alloy Inorganic materials 0.000 title claims description 4
- 238000001953 recrystallisation Methods 0.000 claims abstract description 18
- 238000010438 heat treatment Methods 0.000 claims abstract description 17
- 239000000956 alloy Substances 0.000 claims abstract description 15
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 14
- 238000009749 continuous casting Methods 0.000 claims abstract description 6
- 238000005482 strain hardening Methods 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims abstract description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 2
- 238000007711 solidification Methods 0.000 claims description 2
- 230000008023 solidification Effects 0.000 claims description 2
- 239000010959 steel Substances 0.000 claims description 2
- 229910003271 Ni-Fe Inorganic materials 0.000 abstract description 6
- 239000002184 metal Substances 0.000 abstract description 4
- 229910052751 metal Inorganic materials 0.000 abstract description 4
- 238000005266 casting Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 3
- 238000000034 method Methods 0.000 description 10
- 238000007796 conventional method Methods 0.000 description 6
- 230000035699 permeability Effects 0.000 description 5
- 239000000463 material Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 239000007921 spray Substances 0.000 description 2
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- 229910018499 Ni—F Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Continuous Casting (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明はＮｉ−Ｆｅの合金の製造方法に関し。[Detailed description of the invention] [Industrial application field] The present invention relates to a method for producing a Ni-Fe alloy.
特にＮｉ−Ｆｅの合金を発熱鋳型を有する連続鋳造法で
製造する方法に関するものである。In particular, the present invention relates to a method for manufacturing a Ni-Fe alloy by a continuous casting method using a heat-generating mold.
〔従来従術と発明が解決すべき問題点〕従来のＮｉ−Ｆ
ｅの系合金の製造方法は９本合金を溶解後インゴットに
鋳造し、熱間加工、冷間加工により所定の寸法に加工さ
ｎる。そのため高い透磁率（μｍ）、高い角型比（Ｂｒ
／Ｂ １ｏ ）を得ようとする場合には高い冷間加工率
（９０％以上）を材料に付与する方法が一般的にとられ
ている。即ち、従来の加工方法においては、低い加工率
では高透磁率、高角型比という優れた磁気的性質を付与
することはできない。ここにμｍは最大透磁率、Ｂｒは
残留磁束密度＋ Ｂ１０は外部磁界１０（６ｅ）におけ
る磁束密度をしめす。[Problems to be solved by conventional techniques and the invention] Conventional Ni-F
The method for manufacturing the alloys of series e is as follows: nine alloys are melted, cast into an ingot, and processed into predetermined dimensions by hot working and cold working. Therefore, high magnetic permeability (μm) and high squareness ratio (Br
/B 1o ), a method of imparting a high cold working rate (90% or more) to the material is generally used. That is, in conventional processing methods, excellent magnetic properties such as high magnetic permeability and high squareness ratio cannot be imparted at low processing rates. Here, μm is the maximum magnetic permeability, Br is the residual magnetic flux density + B10 is the magnetic flux density in the external magnetic field 10 (6e).
したがって本発明は、冷間加工率が低くても高透磁率、
高角型比の優れた磁気特性を付与することのできるＮｉ
−Ｆｅ合金の製造方法を提供するにある。Therefore, the present invention provides high magnetic permeability and
Ni can provide excellent magnetic properties with high squareness ratio
-Providing a method for producing an Fe alloy.
本発明は上記の問題点を解決するために、鋳型として後
に説明する発熱鋳型を用い、さらに熱処理条件を適正に
選択して上記の目的を達成するようにしたものである。In order to solve the above-mentioned problems, the present invention uses a heat-generating mold, which will be described later, as a mold, and furthermore, appropriately selects heat treatment conditions to achieve the above-mentioned object.
すなわち本発明によれば、 Ｎｉ ３５−ｓｓ重ｉｔチ
ー残部Ｆｅよシなる組成の合金を、一端から溶鋼を供給
し、他端から鋳片を連続的に得るため鋳型出口の内壁を
、内蔵する発熱体で凝固温度以上に保ちながら連続鋳造
する製造方法において、前記鋳片に一軸異方性を付与し
、得られた鋳片のまま、もしくは冷間加工を施した後。That is, according to the present invention, an alloy having a composition of Ni 35-ss heavy and the remainder Fe is supplied with molten steel from one end and an inner wall of the mold outlet is built in to continuously obtain slabs from the other end. In a production method in which continuous casting is performed while maintaining the temperature above the solidification temperature using a heating element, uniaxial anisotropy is imparted to the slab, and the resulting slab is used as it is or after cold working.
一次再結晶温度以上、二次再結晶温度未満の温度で熱処
理を行うことを特徴とするＮｉ−Ｆｅ合金の製造方法が
得られる。A method for producing a Ni-Fe alloy is obtained, which is characterized in that heat treatment is performed at a temperature higher than the primary recrystallization temperature and lower than the secondary recrystallization temperature.
尚９本発明で規定している再結晶温度は。9. The recrystallization temperature specified in the present invention is:
の温度は溶解条件や鋳造条件による。微量不純物（酸素
、窒素、介在物）の童により変化することは一般的に認
められることであるが、いずれにしても一次再結晶温度
以上、二次再結晶温度未満の温度で熱処理することが磁
気特性な改善させるために必要である。The temperature depends on the melting and casting conditions. It is generally accepted that trace impurities (oxygen, nitrogen, inclusions) change depending on the composition, but in any case, heat treatment at a temperature higher than the primary recrystallization temperature and lower than the secondary recrystallization temperature is recommended. Necessary to improve magnetic properties.
はじめに本発明において使用する発熱鋳型を用いた鍛造
装置について説明する。First, a forging device using a heat-generating mold used in the present invention will be explained.
第１図は特公昭５５−４６２６５号で開示されている装
置の第１図をそのまた示した図であり。FIG. 1 is a diagram showing another version of FIG. 1 of the apparatus disclosed in Japanese Patent Publication No. 55-46265.
タンプジュロからの溶湯７は、鋳型１を通って下方に流
れるが、鋳型１の出口の内壁面を発熱体２により加熱し
て溶湯が鋳型１の内では凝固殻を形成せず、鋳型の出口
を出ると同時に凝固殻９の形成が開始されるようになっ
ている。従って鋳型中空部の断面形状を最終製品の断面
形状を同じにするか相似形にしておけば、得られる鋳塊
１０は加工することなく又は僅かの加工で製品とするこ
とができ、而も表面に亀裂が生じることもない。なお４
はスプレーノズル、５は冷却水、８はピンチローラであ
る。The molten metal 7 from the tampjuro flows downward through the mold 1, but the inner wall surface of the outlet of the mold 1 is heated by the heating element 2, so that the molten metal does not form a solidified shell in the mold 1 and the outlet of the mold is heated. Formation of the solidified shell 9 is started at the same time as it exits. Therefore, by making the cross-sectional shape of the mold hollow part the same as or similar to the cross-sectional shape of the final product, the obtained ingot 10 can be made into a product without any processing or with a small amount of processing, and the surface No cracks will occur. Note 4
5 is a spray nozzle, 5 is a cooling water, and 8 is a pinch roller.
次に実施例につき説明する。Next, an example will be explained.
実施例−１
５０％Ｎｉ−０，５％Ｍｎ−０，２％Ｓｉ−残Ｐａ（上
記チは全て重量％）の合金を上記の発熱鋳型により連φ
続鋳造さ、れた５、５Ｉの鋳片に９５％の冷間加工率を
付与し、熱処理条件を変えた場合の磁気特性を表−１に
示す。Example-1 An alloy of 50% Ni-0.5% Mn-0.2% Si-remaining Pa (all the above values are by weight) was continuously cast in the above-mentioned exothermic mold. Table 1 shows the magnetic properties when the slab was given a cold working rate of 95% and the heat treatment conditions were changed.
（表−１） この合金では６００℃が一次再結晶温度で。(Table-1) For this alloy, 600°C is the primary recrystallization temperature.
１０５０℃が二次再結晶温度であり９表−１で明らかな
ように、６００℃以上、１０５０℃以下で熱処理を行う
ことによりμ、は５０Ｘ１０’以上で角型比１が８０チ
以上を同時に満足できる。1050℃ is the secondary recrystallization temperature, and as is clear from Table 9-1, by performing heat treatment at 600℃ or higher and 1050℃ or lower, μ is 50×10′ or higher and the squareness ratio 1 is 80× or higher at the same time. Satisfied.
なお、比較例として従来のインゴット法によって得た鋳
片と同時に熱処理した時のデータも併せて記している。As a comparative example, data obtained when the slab was heat treated at the same time as the slab obtained by the conventional ingot method is also shown.
本発明は従来法に比し、明らかにμｍでも角型比でも格
段に優れていることが分かる。即ち。It can be seen that the present invention is clearly much superior to the conventional method in terms of μm and squareness ratio. That is.
従来法でも６００−１０５０℃での熱処理により。Conventional methods also include heat treatment at 600-1050°C.
μｍも角型比も向上はする。しかし２μｍが５０×１０
５以上、角型比８０％以上を同時に満足するには２本発
明で言う、一次再結晶温度以上、二次再結晶温度未満で
の熱処理が必要である事が明らかである。Both μm and squareness ratio improve. However, 2μm is 50×10
5 or higher and squareness ratio of 80% or higher at the same time, it is clear that heat treatment at a temperature higher than the primary recrystallization temperature and lower than the secondary recrystallization temperature, which is referred to in the present invention, is required.
なお−次回結晶温度未満の熱処理温度においても、従来
法より優れた磁気特性が得られるものの、このような低
温で処理した場合材料の硬さが高く、二次加工（曲げ、
潰し）が困難となり実用的に不適である。又、二次再結
晶温度以上では従来法の方がむしろ磁気特性が優れてい
る。Although magnetic properties superior to conventional methods can be obtained even at heat treatment temperatures below the next crystallization temperature, the hardness of the material increases when treated at such low temperatures, making secondary processing (bending, bending,
This makes it difficult to crush (crush), making it practically unsuitable. Further, at temperatures above the secondary recrystallization temperature, the conventional method has better magnetic properties.
なお上記の試料であるＮ １−Ｆｅ合金にはＭｎ。Note that the above sample N1-Fe alloy contains Mn.
Ｓｌが含まれているが、この様なＮｉ−Ｆｅ合金には一
般的に脱酸剤、脱硫剤、特性改善の為の添加元素として
、上記のほかにＣ，Ａｌ、 Ｔｉ。Although it contains Sl, such Ni-Fe alloys generally contain C, Al, and Ti in addition to the above as additive elements for deoxidizing agents, desulfurizing agents, and property improvement.
Ｚｒ、Ｃａ、Ｍｇ、ＭＭ、Ｃｒ、Ｍｏ、Ｃｕ、Ｎｄ、Ｔ
ａ等が添加されている。しかしながらこの様な添加元素
はＮｉ、Ｆθに比べ僅かであり、上記の一次再結晶温度
以上、二次再結晶温度以下という条件を変えるものでは
ない。Zr, Ca, Mg, MM, Cr, Mo, Cu, Nd, T
A etc. are added. However, such additive elements are small compared to Ni and Fθ, and do not change the above-mentioned conditions of being above the primary recrystallization temperature and below the secondary recrystallization temperature.
実施例−２
表−２に示すような組成のＮｉ−Ｆｅ０糸合金５種類を
発熱鋳型を有する連続鋳造法で鋳片を得た。比較のため
に従来のインゴット法による鋳片も各々用意した。Example 2 Five types of Ni-Fe0 yarn alloys having compositions shown in Table 2 were obtained by continuous casting using a heat-generating mold. For comparison, slabs produced using the conventional ingot method were also prepared.
これらの鋳片を冷間加工率を０％、６０％、６０％。These slabs were cold worked at a rate of 0%, 60%, and 60%.
（右）の特性な表−５に従来のインゴット法によるもの
と併せて示した。(Right) The characteristics are shown in Table 5 along with those made by the conventional ingot method.
（表−３）
牡下永日
熱処理を施すことにより各々の合金の特性向上が図られ
ていることが明らかであるが９本発明によれば９μｍも
Ｂｒ／Ｂ、。も大幅に向上し、従来インゴット法材を処
理したものよりも極めて大きく特性改善が見られる。と
りわけ、従来のインゴット法では加工率９０％以上にし
なければ得られないμｔｎａ Ｉ３ｒ／Ｂ１１）が発熱
鋳型を有する連続鋳造法による鋳片であれば、加工率が
小さくても、極端に言えば０％の加工率であっても得ら
れる。この現象は発熱鋳型内で鋳片が凝固する際、鋳片
が発熱鋳型の外で水冷却されているため、結晶が鋳造方
向に揃って凝固することに起因している。すなわち−軸
異方性を付与することによる。加工率が小さくできると
言うことは、量産工程では装置がより簡易なものに、又
加工時間の効率化を図かることになり、コスト面で極め
て合理的なものとなり有利である。(Table 3) It is clear that the properties of each alloy are improved by applying the Oshita Eiichi heat treatment, but according to the present invention, the Br/B ratio is as high as 9 μm. The characteristics have also been significantly improved, and the properties have been significantly improved compared to those processed using conventional ingot method materials. In particular, μtna I3r/B11), which cannot be obtained with the conventional ingot method unless the processing rate is 90% or more, can be reduced to 0 even if the processing rate is small, if the slab is produced by a continuous casting method with a heat-generating mold. % processing rate. This phenomenon is caused by the fact that when the slab solidifies in the heat-generating mold, the crystals solidify in alignment with the casting direction because the slab is water-cooled outside the heat-generating mold. That is, by imparting -axis anisotropy. The fact that the processing rate can be reduced is advantageous in the mass production process because the equipment can be simpler and the processing time can be made more efficient, making it extremely rational in terms of cost.
以上１本発明について説明したが２発熱鋳型を用いて鍛
造し、−次頁結晶温度（６００℃）以上。1. The present invention has been described above, but 2. It is forged using an exothermic mold, and the crystal temperature (600° C.) or higher.
二次再結晶温度（１０５０’Ｃ）未満で熱処理すること
により、従来法に比し低加工率側で透磁率が約２〜５倍
、角形比で約１．１〜１．６倍の優れた磁気特性を得る
ことができ、最終製品を得るまでのコストが、装置の面
から又時間の面から大きく低減される。By heat-treating below the secondary recrystallization temperature (1050'C), magnetic permeability is approximately 2 to 5 times better at low processing rates and approximately 1.1 to 1.6 times better in squareness than conventional methods. The cost of obtaining the final product can be greatly reduced in terms of equipment and time.
第１図は本発明による製造方法において使用する鍛造装
置の構成の断面を示す図である。
記号の説明：１は鋳型、２は発熱体、４にスプレーノズ
ル、６はタンプシュ、７は溶湯、８はピンチロール、９
は凝固殻、１０は鋳塊をそれぞれあられしている。FIG. 1 is a cross-sectional view of the configuration of a forging device used in the manufacturing method according to the present invention. Explanation of symbols: 1 is the mold, 2 is the heating element, 4 is the spray nozzle, 6 is the tamp, 7 is the molten metal, 8 is the pinch roll, 9
10 indicates the solidified shell, and 10 indicates the ingot.
Claims (1)
、一端から溶鋼を供給し、他端から鋳片を連続的に得る
ための鋳型出口の内壁を、内蔵する発熱体で凝固温度以
上に保ちながら連続鋳造する製造方法において、前記鋳
片に一軸異方性を付与し、得られた鋳片のまま、もしく
は冷間加工を施した後、一次再結晶温度以上、二次再結
晶温度未満の温度で熱処理を行うことを特徴とするＮｉ
−Ｆｅ合金の製造方法。An alloy with a composition of 35-85% Ni by weight and the balance Fe is supplied with molten steel from one end and the inner wall of the mold outlet for continuously obtaining slabs from the other end is kept above the solidification temperature by a built-in heating element. In the manufacturing method of continuous casting, the slab is given uniaxial anisotropy, and the slab is cast as is or after cold working, at a temperature higher than the primary recrystallization temperature and lower than the secondary recrystallization temperature. Ni characterized by heat treatment at high temperature
-Method for producing Fe alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26239085A JPS62124264A (en) | 1985-11-25 | 1985-11-25 | Manufacture of ni-fe alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26239085A JPS62124264A (en) | 1985-11-25 | 1985-11-25 | Manufacture of ni-fe alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62124264A true JPS62124264A (en) | 1987-06-05 |
| JPH0332628B2 JPH0332628B2 (en) | 1991-05-14 |
Family
ID=17375098
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP26239085A Granted JPS62124264A (en) | 1985-11-25 | 1985-11-25 | Manufacture of ni-fe alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62124264A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111318658A (en) * | 2020-03-24 | 2020-06-23 | 山西太钢不锈钢股份有限公司 | Invar alloy and continuous casting production method thereof |
-
1985
- 1985-11-25 JP JP26239085A patent/JPS62124264A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111318658A (en) * | 2020-03-24 | 2020-06-23 | 山西太钢不锈钢股份有限公司 | Invar alloy and continuous casting production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0332628B2 (en) | 1991-05-14 |
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