JPS63161146A - Cr-ni steel bar for magnetic graduation - Google Patents
Cr-ni steel bar for magnetic graduationInfo
- Publication number
- JPS63161146A JPS63161146A JP61314507A JP31450786A JPS63161146A JP S63161146 A JPS63161146 A JP S63161146A JP 61314507 A JP61314507 A JP 61314507A JP 31450786 A JP31450786 A JP 31450786A JP S63161146 A JPS63161146 A JP S63161146A
- Authority
- JP
- Japan
- Prior art keywords
- magnetic
- flux density
- magnetic flux
- saturation magnetic
- steel
- 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
- 230000005291 magnetic effect Effects 0.000 title claims abstract description 78
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 13
- 239000010959 steel Substances 0.000 title claims abstract description 13
- 230000004907 flux Effects 0.000 claims abstract description 38
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims abstract 3
- 239000000463 material Substances 0.000 abstract description 15
- 238000005491 wire drawing Methods 0.000 abstract description 15
- 229910001566 austenite Inorganic materials 0.000 abstract description 2
- 238000011156 evaluation Methods 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 abstract description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 abstract 1
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000126 substance Substances 0.000 abstract 1
- 238000001514 detection method Methods 0.000 description 7
- 238000012545 processing Methods 0.000 description 7
- 230000007423 decrease Effects 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 230000005307 ferromagnetism Effects 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 230000005294 ferromagnetic effect Effects 0.000 description 3
- 239000000696 magnetic material Substances 0.000 description 3
- 238000003754 machining Methods 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000001678 irradiating effect Effects 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Landscapes
- Measurement Of Length, Angles, Or The Like Using Electric Or Magnetic Means (AREA)
- Transmission And Conversion Of Sensor Element Output (AREA)
- Hard Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、メカトロニクス分野で用いられる磁気目盛用
網棒の改良に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to an improvement of a magnetic scale mesh bar used in the mechatronics field.
（従来の技術及びその問題点）
近年メカトロニクスの発展に伴い第６図（イ）に示す様
な位置検出機構として磁気目盛が使用される様になった
。この磁気目盛用材料として要求される特性は、工業的
に容易に第６図（イ）に示す如き強磁性、非磁性の組合
せが実現できることである。なお、第６図（イ）中１は
母材部、２は溶体化（非磁性）部、３は位置検出センサ
ーを示す。(Prior art and its problems) With the development of mechatronics in recent years, magnetic scales have come to be used as position detection mechanisms as shown in FIG. 6(a). The characteristics required for this material for magnetic scales are that the combination of ferromagnetism and non-magnetism as shown in FIG. 6(a) can be easily realized industrially. In FIG. 6(a), 1 indicates a base material part, 2 a solution-treated (non-magnetic) part, and 3 a position detection sensor.
この具体的方法として、例えば、特開昭５８−７５１７
号公報に示される様に金属材の表面に金属化合物を化学
メンキした後、レーザー等の粒子線により加熱して磁気
的変質部を所定間隔で形成する様にしたものが知られて
いる。また、特開昭５７−１６３０９号公報には、金属
材料表面に高エネルギービームを照射して局部的に熱処
理し磁気的に変質させて目盛を付ける方法が示されてい
る。As a specific method for this, for example, JP-A-58-7517
As shown in the above publication, a method is known in which the surface of a metal material is chemically coated with a metal compound and then heated with a particle beam such as a laser to form magnetically altered parts at predetermined intervals. Furthermore, Japanese Patent Laid-Open No. 57-16309 discloses a method of applying a scale by irradiating the surface of a metal material with a high-energy beam, locally heat-treating the surface, and magnetically altering the material.
しかし、これらは目盛部と基体部の磁気特性の差が小さ
くて高価な検出装置が必要となったり、あるいは検出の
信顛性が低いといった欠点があった。However, these have drawbacks such as a small difference in magnetic properties between the scale portion and the base portion, requiring an expensive detection device, or low detection reliability.
そこで、この対策としてＦｅ２５重景％、Ｎｉ７５重量
％合金等の非常に高価な磁性材料を適用する例も示され
ているが、これは高価なだけであって強度や耐摩耗性は
あまり望めず、用途上の制約が多い上、磁気特性も完全
とは言い難い。Therefore, as a countermeasure to this problem, examples have been shown of applying very expensive magnetic materials such as alloys with 25% Fe and 75% Ni by weight, but this is only expensive and does not offer much strength or wear resistance. , there are many restrictions in terms of use, and the magnetic properties are also far from perfect.
一方、ある種のオーステナイト系ステンレス鋼は溶体化
状態では非磁性でかつ冷間加工により加工誘起変態が起
こり、強磁性化することが知られており、この特性を利
用すれば比較的簡単に磁気目盛が実現できる可能性があ
る。On the other hand, it is known that certain types of austenitic stainless steels are non-magnetic in the solution state, but undergo a strain-induced transformation during cold working and become ferromagnetic. There is a possibility that a scale can be realized.
本発明の目的は、この現象に着想を得て磁気目盛用材料
としての性能を高めるために成分を改良し、それによっ
て安価で強度が高く、かつ磁気目盛性能に優れた磁気目
盛用鋼棒を提供することにある。The purpose of the present invention is to improve the composition of the material to improve its performance as a material for magnetic scales based on this phenomenon, thereby producing a steel rod for magnetic scales that is inexpensive, has high strength, and has excellent magnetic scale performance. It is about providing.
（問題点を解決するための手段）
本発明は、Ｃｒ、Ｎｉを含み、あるいはさらにＭｏを含
む準安定オーステナイト鋼において、Ｍｏ□４Ｌ３ ４
６２ Ｘ （Ｃ＋Ｎ） ９．２Ｓ ｔ ８．ＩＭ
ｎ−１３，７Ｃｒ −９，５Ｎ ｉ −１８，５Ｍ ｏ
なる式で表されるＭｌ、値が１５℃以上で、さらに２Ｎ
ｉ＋１００Ｘ （Ｃ＋Ｎ） −Ｃｒ≧２．０の条件を満
足する成分からなり、飽和磁束密度が５ＫＧ以上、１２
ＫＧ以下になる様冷間伸線し、局部を加熱溶体化するこ
とで当該箇所を飽和磁束密度０．１ＫＧ以下の非磁性と
したことを要旨とするものである。(Means for Solving the Problems) The present invention provides a metastable austenitic steel containing Cr, Ni, or further containing Mo.
62 X (C+N) 9.2S t 8. IM
n-13,7Cr -9,5N i -18,5Mo
Ml expressed by the formula, when the value is 15°C or more, and further 2N
i+100X (C+N) - Cr≧2.0, saturation magnetic flux density is 5KG or more,
The gist of the method is to cold draw the wire so that the magnetic flux density becomes 0.1 KG or less, and heat the local part to form a solution, thereby making the part non-magnetic with a saturation magnetic flux density of 0.1 KG or less.
磁気目盛用鋼としては溶体化で完全な非磁性を得る一方
で、冷間加工で強磁性化をできるだけ発達させなければ
優れた特性は得られない。そこで、本発明者等はこれを
実現するための材料成分を詳細に研究した結果、この非
磁性化と強磁性化は矛盾するもので、これを実現するに
は微量元素に至たるまで適切に制御しなければならない
ことを見出した。具体的に磁気目盛材料として必要な特
性を述べると、その骨子とするところは以下の通りであ
る。As a steel for magnetic scales, while it can be made completely non-magnetic by solution treatment, excellent properties cannot be obtained unless ferromagnetism is developed as much as possible by cold working. As a result of detailed research into material components to achieve this, the inventors found that non-magnetization and ferromagnetization are contradictory, and in order to achieve this, it is necessary to properly select trace elements. I found that I had to control it. Specifically, the characteristics necessary for a magnetic scale material are as follows.
■母材部は強磁性体で５ＫＧ以上の飽和磁束密度を有す
ること。■The base material must be ferromagnetic and have a saturation magnetic flux density of 5KG or more.
■溶体化部は非磁性体であり、飽和磁束密度０．１ＫＧ
以下であること。■The solution-treated part is a non-magnetic material, and the saturation magnetic flux density is 0.1KG.
Must be below.
本発明ではこれらの特性を得るために、前述したように
各諸元の限定を行った。以下に、その限定理由について
詳細に述べる。In the present invention, in order to obtain these characteristics, each specification is limited as described above. The reasons for this limitation will be described in detail below.
前述の如く、磁気目盛は強磁性部と非磁性部の磁気特性
の差を位置検出に利用するものである。As mentioned above, the magnetic scale utilizes the difference in magnetic properties between the ferromagnetic part and the non-magnetic part for position detection.
そこで前記の所要特性を得るためには、この強磁性と非
磁性を夫々ある一定レベルに保つ必要が生れる。第１図
に母材の飽和磁束密度と磁気センサーの往復誤差の関係
を示す。ここで磁気センサーの往復（出力）誤差とは第
６図（ロ）に示す如くセンサーまたは磁気目盛材を往復
させたときの「出力波形におけるピーク電圧」の変化量
（ピーク出力差、△Ｖ）を計測し、そのときのピーク電
圧幅（ピーク出力値、■）の〃で除してパーセントで表
示したものである。すなわち、往復（出力）誤差＝〔△
ｖ／ （ｖ／２））ｘｌｏＯ％と表されるものである。Therefore, in order to obtain the above-mentioned required characteristics, it is necessary to maintain the ferromagnetism and nonmagnetism at a certain level. Figure 1 shows the relationship between the saturation magnetic flux density of the base material and the reciprocating error of the magnetic sensor. Here, the reciprocating (output) error of a magnetic sensor is the amount of change in the "peak voltage in the output waveform" (peak output difference, △V) when the sensor or magnetic scale material is reciprocated as shown in Figure 6 (b). is measured, divided by the peak voltage width (peak output value, ■) at that time, and expressed as a percentage. In other words, round trip (output) error = [△
v/(v/2))xloO%.
そして、この数値は位置精度に極めて大きな影響がある
ので、磁気目盛にとって重要な特性である。This numerical value has an extremely large effect on positional accuracy, and is therefore an important characteristic for magnetic scales.
しかして、往復誤差は４．０％以下が実用許容範囲であ
るが、これを維持するには第１図より飽和磁束密度が５
ＫＧ以上必要なことが判る。もちろん前述の通り磁気目
盛の特性は、母材の強磁性だけでなく、溶体化部の非磁
性の程度にも影響され両者の差が大きい程、特性は良く
なる（誤差が小さくなる）。Therefore, a reciprocating error of 4.0% or less is a practical allowable range, but in order to maintain this, the saturation magnetic flux density is 5%, as shown in Figure 1.
It turns out that more than KG is required. Of course, as mentioned above, the characteristics of the magnetic scale are influenced not only by the ferromagnetism of the base material but also by the degree of nonmagnetism of the solution-treated part, and the larger the difference between the two, the better the characteristics (the smaller the error).
第１図は、溶体化部の飽和磁束密度が５０〜７０Ｇで、
はぼ完全に非磁性化されている例である。この様に、溶
体化部の非磁性が完全な場合、母材部の飽和磁束密度が
変化するとセンサー出力は一定であるが、往復誤差は増
加につれて減少する。すなわち、磁気センサーの往復誤
差を実用許容範囲の４％以下に押えるためには、母材部
の飽和磁束密度を５ＫＧ以上にする必要があり、本発明
ではかかる値に限定した。Figure 1 shows that the saturation magnetic flux density of the solution treatment section is 50 to 70G.
This is an example of completely non-magnetic material. In this manner, when the solution-treated part is completely non-magnetic, the sensor output remains constant as the saturation magnetic flux density of the base metal part changes, but the reciprocating error decreases as it increases. That is, in order to suppress the reciprocating error of the magnetic sensor to 4% or less, which is the practical allowable range, it is necessary to make the saturation magnetic flux density of the base material part 5 KG or more, and the present invention is limited to this value.
一方、第２図に往復誤差に及ぼす溶体化部の飽和磁束密
度の影響を示す。同図から明らかな様に、溶体化部の飽
和磁束密度が増加して非磁性が保れなくなると、センサ
ー出力が低下し、その結果、往復誤差が大きくなる。往
復誤差を実用許容範囲である４、０％以下にするには、
溶体化部の飽和磁束密度を１００ Ｇ （０，１ＫＧ）
以下にすることが必要であり、本発明ではかかる値に限
定した。On the other hand, FIG. 2 shows the influence of the saturation magnetic flux density of the solution-treated section on the reciprocating error. As is clear from the figure, when the saturation magnetic flux density of the solution-treated portion increases and nonmagnetism cannot be maintained, the sensor output decreases, and as a result, the reciprocating error increases. To reduce the reciprocating error to less than 4.0%, which is the practical allowable range,
The saturation magnetic flux density of the solution treatment part is 100 G (0.1 KG)
It is necessary to set the value below, and the present invention is limited to this value.
次に、本発明ではこの様な磁気特性を実現し得る鋼種成
分を限定した。Next, in the present invention, the steel type components that can realize such magnetic properties are limited.
本発明者等はＣｒ−Ｎｉ系準安定オーステナイトの加工
に対する安定性の評価指標として使われるＭ０値を使っ
て、溶体化、伸線加工によって得られる磁気特性につい
て整理した。その結果を第３図及び第４図に示す。The present inventors organized the magnetic properties obtained by solution treatment and wire drawing using the M0 value, which is used as an evaluation index of the stability of Cr-Ni based metastable austenite against processing. The results are shown in FIGS. 3 and 4.
Ｍｏ値は４１３−４６２ Ｘ （Ｃ＋Ｎ） −９，２５
ｉ −８，１Ｍ ｎ −１３，７Ｃｒ −９，５Ｎｉ
−１８，５Ｍ ｏなる式で表されるが、第３図に伸線
後の飽和磁束密度がＭＤ値によって変化する様子を、ま
た第４図に伸線加工によって飽和磁束密度が増加する様
子を夫々示す。Mo value is 413-462 X (C+N) -9,25
i -8,1M n -13,7Cr -9,5Ni
Figure 3 shows how the saturation magnetic flux density after wire drawing changes depending on the MD value, and Figure 4 shows how the saturation magnetic flux density increases due to wire drawing. Show each.
第３図よりＭｏ値が１５℃以下の場合には加工度を上げ
ても必要な５ＫＧを確保できないことが判る（同様のこ
とは第４図からも判る）、また、第４図よりＭ、値が１
２℃の場合には伸線加工による飽和磁束密度の上昇が４
．５ＫＧ程度で頭打ちになっており、必要な５ＫＧを確
保できないことが判る。この様な理由から本発明ではＭ
Ｄ値を１５℃以上に限定した。It can be seen from Fig. 3 that if the Mo value is 15°C or less, the required 5 kg cannot be secured even if the processing degree is increased (the same can be seen from Fig. 4). Also, from Fig. 4, M, value is 1
At 2℃, the increase in saturation magnetic flux density due to wire drawing is 4
．． It has reached a plateau at around 5KG, indicating that it is not possible to secure the necessary 5KG. For these reasons, in the present invention, M
The D value was limited to 15°C or higher.
また、第４図に示す様に冷間伸線により飽和磁束密度が
増加して１２ＫＧを超えると加工割れが発生する。これ
は加工誘起マルテンサイトの量が許容限界を超えて発生
し、割れの原因になったためでありこのような理由から
本発明では飽和磁束密度の上限を１２ＫＧに限定した。Further, as shown in FIG. 4, when the saturation magnetic flux density increases due to cold wire drawing and exceeds 12 KG, processing cracks occur. This is because the amount of deformation-induced martensite exceeds the allowable limit and causes cracking. For this reason, the upper limit of the saturation magnetic flux density is limited to 12 KG in the present invention.
第５図に溶体化状態での飽和磁束密度がＮｉ。Figure 5 shows the saturation magnetic flux density of Ni in the solution state.
Ｃｒ、Ｃ，Ｎによって変化する様子を示す。溶体化状態
での飽和磁束密度の増加は主にδフェライトの発生に起
因する。Ｎｉ、Ｃ，Ｎは減少するとδフェライトの発生
を促進するし、一方Ｃｒは減少するとδフェライトの発
生は逆に減少する。この溶体化状態でのδフエライト発
生による飽和磁束密度の変化を整理する指標として
２Ｎ ｉ ＋ １００ Ｘ （Ｃ＋Ｎ） −Ｃｒを用い
た。その結果が第５図である。同図から明らかな様に、
必要とする非磁性確保レベルである１ ００Ｇ （０，
１ＫＧ）以下を確保するには、２Ｎｉ ＋１００ Ｘ
（Ｃ＋Ｎ）−Ｃｒの値が２．０以上であることを要する
。It shows how it changes depending on Cr, C, and N. The increase in saturation magnetic flux density in the solution state is mainly due to the generation of δ ferrite. When Ni, C, and N decrease, they promote the generation of δ ferrite, while when Cr decreases, the generation of δ ferrite decreases. 2N i + 100 X (C+N) - Cr was used as an index for organizing changes in saturation magnetic flux density due to the generation of δ ferrite in this solution state. The result is shown in FIG. As is clear from the figure,
100G (0,
1KG) or less, 2Ni +100X
The value of (C+N)-Cr is required to be 2.0 or more.
この様な理由から、本発明では２Ｎｉ＋１００Ｘ （Ｃ
＋Ｎ）−Ｃｒの値を２．０以上に限定した。For these reasons, in the present invention, 2Ni+100X (C
+N)-Cr value was limited to 2.0 or more.
（実施例）
本発明の効果を実施例により説明する。本実施例では下
記表に掲げる１Ｉｉｌ１１．５．８．１１．１４．１６
．１９及び２１〜２７の鋼を１５０ ｋｇ真空溶解炉で
溶製して３２φの棒材に熱間鍛造した後、２５φに外削
し試験に供した。(Example) The effects of the present invention will be explained by examples. In this example, 1Iil11.5.8.11.14.16 listed in the table below
．． Steel Nos. 19 and 21 to 27 were melted in a 150 kg vacuum melting furnace, hot forged into a 32φ bar, and then externally machined to a 25φ bar for testing.
実施例？＆Ｌ１〜４では、Ｍ、値が１２．３と本発明範
囲を下回っている。このため、溶体化状態の飽和磁束密
度は２０Ｇ以下と十分に低い値を保っているが、伸線後
では、加工度を５７％まで上げても４４２０Ｇにしかな
らず、これ以上加工しても増加する傾向が認められない
。したがって、各加工度に伸線後、レーザーで溶体化目
盛処理後、第６図に示す検出装置により精度を測定した
結果、いずれも５ＫＧに不足しているため、往復誤差は
５．４％〜１４．５％と実用許容範囲の４．０％を超え
ている。Example? In &L1-4, the M value is 12.3, which is below the range of the present invention. For this reason, the saturation magnetic flux density in the solution state is kept at a sufficiently low value of 20G or less, but after wire drawing, even if the processing degree is increased to 57%, it will only reach 4420G, and it will increase even if processing is performed further. No trend observed. Therefore, after wire drawing to each degree of processing and after processing the solution scale using a laser, the accuracy was measured using the detection device shown in Figure 6, and as a result, the accuracy was less than 5 kg in both cases, so the reciprocating error was 5.4% ~ 14.5%, which exceeds the practical allowable range of 4.0%.
実施例１’ｈ５〜１５ではＭ、値が１８．０〜６４．５
といずれも本発明範囲の中にある。しかし、実施例光５
．８においては冷間伸線による飽和磁束密度の上昇が夫
々３０５０Ｇと４５００ＧＬかなく、本発明範囲の５０
００Ｇに達していない。このため往復誤差は夫々１２．
１％、５．４％と実用許容範囲の４．０％を超えている
。In Example 1'h5-15, M value is 18.0-64.5
Both are within the scope of the present invention. However, Example Light 5
．． 8, the increase in saturation magnetic flux density due to cold wire drawing was only 3050G and 4500GL, respectively, and 50G, which is within the range of the present invention.
It has not reached 00G. Therefore, the round trip error is 12.
1% and 5.4%, exceeding the practical allowable range of 4.0%.
一方、実施例阻１３．１５では冷間伸線後の飽和磁束密
度が夫々１３５００Ｇ、１３１００Ｇと本発明範囲の１
２０００Ｇを超えたため、加工割れが発生している。こ
れ以外の実施側石６．７．９．１０．１１．１２．１４
ではＭＤ値、２Ｎｉ＋１００Ｘ （Ｃ＋Ｎ）−Ｃｒ、及
び伸線後の飽和磁束密度のいずれもが本発明範囲にあり
往復誤差も実用許容範囲の４．０％以下に収まっている
。On the other hand, in Example 13.15, the saturation magnetic flux density after cold wire drawing was 13,500G and 13,100G, respectively, which was within the range of the present invention.
Because the force exceeded 2000G, machining cracks occurred. Other implementation stones 6.7.9.10.11.12.14
In this case, the MD value, 2Ni+100X (C+N)-Cr, and the saturation magnetic flux density after wire drawing are all within the range of the present invention, and the reciprocating error is also within the practical allowable range of 4.0% or less.
実施例１１＆ｌ１６〜２０では、２Ｎｉ ＋１００Ｘ
（Ｃ＋Ｎ）−Ｃｒの値が１．５〜１．７と本発明範囲を
外れて下回っており、このため溶体化時の飽和磁束密度
が３１０〜４００Ｇと１００Ｇを超えている。In Examples 11 & 16-20, 2Ni +100X
The value of (C+N)-Cr is 1.5 to 1.7, which is outside the range of the present invention, and therefore the saturation magnetic flux density during solution treatment is 310 to 400G, which exceeds 100G.
したがって、往復誤差は１０．１％〜１２．１％と実用
許容範囲の４．０％を大きく超えている。また、実施例
Ｎ１１８．２０では伸線後の飽和磁束密度が夫々１２２
００Ｇと１３０００Ｇと、本発明範囲の１２０００Ｇを
超えたため加工割れが発生している。Therefore, the reciprocating error is 10.1% to 12.1%, which greatly exceeds the practical allowable range of 4.0%. In addition, in Example N118.20, the saturation magnetic flux density after wire drawing was 122, respectively.
00G and 13000G, which exceeded the range of 12000G according to the present invention, caused machining cracks.
実施例光２１〜２５ではＮｉ量を調整し２Ｎｉ＋１ＯＯ
Ｘ （Ｃ＋Ｎ）−ＣｒＯ値を変化させた。In Example Lights 21 to 25, the amount of Ni was adjusted to 2Ni+1OO
The X (C+N)-CrO value was varied.
すなわち、実施例阻２１〜２３では２Ｎｉ＋１０ Ｑｘ
（Ｃ＋Ｎ）−Ｃｒの値が３．２〜３．６と本発明範囲
内にあり、溶体化時の飽和磁束密度が、４０〜５０Ｇと
１００Ｇ以下に収っている。したがって往復誤差も２．
９％〜３．１％と実用許容範囲４％に収っている。一方
、実施例阻２４〜２５では２Ｎｉ＋１００Ｘ （Ｃ＋Ｎ
）−Ｃｒの値は０．５〜１．９と本発明範囲を下回って
おり溶体化時の飽和磁束密度も１３０〜９５０Ｇと１０
０Ｇを超えている。このため往復誤差も５．２％〜１７
．１％と４％を超えてしまっている。That is, in Examples 21 to 23, 2Ni+10Qx
The value of (C+N)-Cr is 3.2 to 3.6, which is within the range of the present invention, and the saturation magnetic flux density during solution treatment is 40 to 50G, which is 100G or less. Therefore, the round trip error is also 2.
It is 9% to 3.1%, which is within the practical allowable range of 4%. On the other hand, in Examples 24 to 25, 2Ni+100X (C+N
)-Cr value is 0.5 to 1.9, which is below the range of the present invention, and the saturation magnetic flux density during solution treatment is 130 to 950G, which is 10
It exceeds 0G. Therefore, the round trip error is also 5.2%~17
．． They have exceeded 1% and 4%.
実施例光２６〜２７ではＭｏを添加した例を示す。いず
れも２Ｎｉ＋１ ｏｏｘ （Ｃ＋Ｎ）−Ｇ及びＭ、値共
本発明範囲を満たしており、往復誤差は３．０％〜３．
２％と許容範囲に収っている。Examples 26 and 27 show examples in which Mo was added. Both values of 2Ni+1 oox (C+N)-G and M satisfy the range of the present invention, and the round-trip error is 3.0% to 3.0%.
2%, which is within the acceptable range.
以上の様に、本発明の請求範囲に従えば、所要の優れた
特性を有する磁気目盛用鋼棒を得ることが出来る。As described above, according to the claims of the present invention, it is possible to obtain a steel bar for magnetic scales having the required excellent characteristics.
（発明の効果）
以上説明したように本発明は、Ｃｒ、Ｎｉを含み、ある
いはさらにＭｏを含む準安定オーステナイト鋼において
、ＭＤ＝４１３ ４６２ Ｘ （Ｃ＋Ｎ） ９．２３
ｉ−８，１Ｍ ｎ −１３，７Ｃｒ −９，５Ｎｉ
−１８，５Ｍ ｏなる式で表されるＭ、値が１５℃以上
で、さらに２ Ｎｉ ＋ １００ Ｘ（Ｃ＋Ｎ）−Ｃｒ
≧２．０の条件を満足する成分からなり、飽和磁束密度
が５ＫＧ以上、１２ＫＧ以下になる様冷間伸線し、局部
を加熱溶体化することで、当該箇所を飽和磁束密度０．
１ＫＧ以下の非磁性とした為、安価で強度が高く、しか
も磁気目盛性能に優れている。(Effects of the Invention) As explained above, the present invention provides a metastable austenitic steel containing Cr, Ni, or further containing Mo, MD=413 462 X (C+N) 9.23
i-8,1M n-13,7Cr-9,5Ni
M expressed by the formula -18,5Mo, the value is 15℃ or higher, and 2Ni + 100X(C+N)-Cr
≧2.0, the wire is cold drawn so that the saturation magnetic flux density is 5 KG or more and 12 KG or less, and the local area is heated to form a solution, so that the saturation magnetic flux density is 0.
Since it is non-magnetic and weighs less than 1KG, it is inexpensive, has high strength, and has excellent magnetic scale performance.
第１図は母材の磁気特性とセンサー往復誤差の関係図、
第２図は溶体化部の磁気特性とセンサー往復誤差の関係
図、第３図は伸線後の飽和磁束密度とＭｏ３０点の関係
図、第４図は伸線加工による飽和磁束密度の増加に及ぼ
すＭ。３０点の影響を示す図面、第５図は成分による溶
体化状態の飽和磁束密度の変化図、第６図（イ）は磁気
目盛による位置検出機構の一例を示す図面、（ロ）はそ
の往復誤差説明図である。
第３１？、 丁４図
ＭＤ うｏｐ−ｃｃ）
Ｒｔ （ｖａ）第５図
ど０）Figure 1 is a diagram of the relationship between the magnetic properties of the base material and the sensor reciprocating error.
Figure 2 shows the relationship between the magnetic properties of the solution-treated part and the sensor reciprocating error, Figure 3 shows the relationship between the saturation magnetic flux density after wire drawing and the Mo30 point, and Figure 4 shows the relationship between the saturation magnetic flux density and the Mo30 point after wire drawing. M exerts. A drawing showing the influence of 30 points, Fig. 5 is a diagram of changes in saturation magnetic flux density in the solution state depending on the components, Fig. 6 (a) is a drawing showing an example of a position detection mechanism using a magnetic scale, and (b) is a diagram showing its reciprocation. It is an error explanatory diagram. 31st? , Figure 4 MD up-cc)
Rt (va) Figure 5 0)
Claims (1)
安定オーステナイト鋼において、Ｍ＿Ｄ＝４１３−４６
２×（Ｃ＋Ｎ）−９．２Ｓｉ−８．１Ｍｎ−１３．７Ｃ
ｒ−９．５Ｎｉ−１８．５Ｍｏなる式で表されるＭｎ値
が１５℃以上で、さらに２Ｎｉ＋１００×（Ｃ＋Ｎ）−
Ｃｒ≧２．０の条件を満足する成分からなり、飽和磁束
密度が５ＫＧ以上、１２ＫＧ以下になる様冷間伸線し、
局部を加熱溶体化することで、当該箇所を飽和磁束密度
０．１ＫＧ以下の非磁性としたことを特徴とする磁気目
盛用鋼棒。(1) In metastable austenitic steel containing Cr, Ni, or further containing Mo, M_D=413-46
2×(C+N)-9.2Si-8.1Mn-13.7C
The Mn value expressed by the formula r-9.5Ni-18.5Mo is 15°C or higher, and further 2Ni+100×(C+N)-
It is made of a component that satisfies the condition of Cr≧2.0, and is cold drawn so that the saturation magnetic flux density is 5KG or more and 12KG or less,
A steel rod for a magnetic scale, characterized in that the local portion is made non-magnetic with a saturation magnetic flux density of 0.1 KG or less by heating it into a solution.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61314507A JPS63161146A (en) | 1986-12-24 | 1986-12-24 | Cr-ni steel bar for magnetic graduation |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61314507A JPS63161146A (en) | 1986-12-24 | 1986-12-24 | Cr-ni steel bar for magnetic graduation |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63161146A true JPS63161146A (en) | 1988-07-04 |
| JPH0475307B2 JPH0475307B2 (en) | 1992-11-30 |
Family
ID=18054119
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61314507A Granted JPS63161146A (en) | 1986-12-24 | 1986-12-24 | Cr-ni steel bar for magnetic graduation |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63161146A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0629711A1 (en) * | 1993-06-18 | 1994-12-21 | Nippondenso Co., Ltd. | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| EP0803582A2 (en) * | 1996-04-26 | 1997-10-29 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| EP2681341A1 (en) * | 2011-03-03 | 2014-01-08 | RLS Merilna Tehnika D.O.O. | Method of manufacturing a magnetic substrate for an encoder |
-
1986
- 1986-12-24 JP JP61314507A patent/JPS63161146A/en active Granted
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6187459B1 (en) | 1993-06-18 | 2001-02-13 | Nippondenso Co., Ltd. | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| US6390443B1 (en) | 1993-06-18 | 2002-05-21 | Nippondenso Co. Ltd. | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| EP0629711A1 (en) * | 1993-06-18 | 1994-12-21 | Nippondenso Co., Ltd. | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| US5865907A (en) * | 1993-06-18 | 1999-02-02 | Nippondenso Co., Ltd | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| EP1061140A1 (en) * | 1993-06-18 | 2000-12-20 | Denso Co., Ltd. | Composite magnetic member, process for producing the member and electromagnetic valve using the member |
| US6143094A (en) * | 1996-04-26 | 2000-11-07 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| EP0803582A2 (en) * | 1996-04-26 | 1997-10-29 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| EP0803582A3 (en) * | 1996-04-26 | 1997-11-12 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| US6949148B2 (en) | 1996-04-26 | 2005-09-27 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| US6521055B1 (en) | 1996-04-26 | 2003-02-18 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| EP1178123A1 (en) * | 1996-04-26 | 2002-02-06 | Denso Corporation | Method of stress inducing transformation of austenite stainless steel and method of producing composite magnetic members |
| EP2681341A1 (en) * | 2011-03-03 | 2014-01-08 | RLS Merilna Tehnika D.O.O. | Method of manufacturing a magnetic substrate for an encoder |
| US10072943B2 (en) | 2011-03-03 | 2018-09-11 | Rls Merilna Tehnika D.O.O. | Method of scale substrate manufacture |
| EP2681341B1 (en) * | 2011-03-03 | 2021-08-11 | RLS Merilna Tehnika D.O.O. | Method of manufacturing a magnetic substrate for an encoder scale |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0475307B2 (en) | 1992-11-30 |
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