JP5365997B2 - Method for producing stainless steel strip for blades - Google Patents
Method for producing stainless steel strip for blades Download PDFInfo
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- JP5365997B2 JP5365997B2 JP2009089763A JP2009089763A JP5365997B2 JP 5365997 B2 JP5365997 B2 JP 5365997B2 JP 2009089763 A JP2009089763 A JP 2009089763A JP 2009089763 A JP2009089763 A JP 2009089763A JP 5365997 B2 JP5365997 B2 JP 5365997B2
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Abstract
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本発明は、例えば、剃刀等の薄い刃物用ステンレス帯鋼の製造方法に関するものである。 The present invention relates to a method for producing a stainless steel strip for a thin blade such as a razor.
剃刀等の薄い刃物用ステンレス鋼としては、従来から多くの提案がなされている。例えば、特開２０００−２７３５８７号公報（特許文献１）には、化学組成を調整することにより、５μｍ以下の微細な炭化物を生成させることにより、刃欠けや刃こぼれ等を生じることなく、刃物の刃先線粗さを、１０μｍ程度の刃物未使用の刃先状態にて維持する事ができ、切れ味持続性が低下せず、切れ味の良好な状態を維持できるステンレス鋼の提案がなされている。 Conventionally, many proposals have been made for stainless steel for thin blades such as razors. For example, in Japanese Patent Laid-Open No. 2000-273587 (Patent Document 1), by adjusting the chemical composition to generate fine carbides of 5 μm or less, there is no blade chipping or blade spilling, etc. There has been proposed a stainless steel that can maintain the cutting edge roughness in an unused cutting edge state of about 10 μm, maintain the sharpness without decreasing the sharpness sustainability.
従来の特許文献１に示される提案は、化学組成の調整によって、炭化物の微細化をはかろうとするものである。
しかしながら、化学組成の調整のみでは、解決しきれない問題がある。具体的には、実際に剃刀等の刃物とする場合においては、例えば、剃刀形状に打抜き加工を施した場合、刃物用ステンレス帯鋼に残留する応力によって、打抜き加工を施した半製品の形状が変形するといった問題がある。特に、この問題は厚さが０．１５ｍｍ以下の薄い刃物用ステンレス帯鋼で顕著となる。
また、半製品の形状の変形を抑制するには、製品幅にスリットした後の工程であって、製品幅にスリットした後の刃物用ステンレス帯鋼については、何等対策がなされていないのが現状である。
本発明の目的は、製品幅にスリットした後の刃物用ステンレス帯鋼に残留する応力を緩和し、加工を施した半製品の形状変形を抑制することができる刃物用ステンレス帯鋼の製造方法を提供する。
The proposal shown in the conventional patent document 1 intends to refine the carbide by adjusting the chemical composition.
However, there is a problem that cannot be solved only by adjusting the chemical composition. Specifically, when a cutting tool such as a razor is actually used, for example, when a punching process is performed on a razor shape, the shape of the semi-finished product subjected to the punching process due to the stress remaining in the stainless steel strip for cutting tool There is a problem of deformation. This problem is particularly noticeable with a thin stainless steel strip for blades having a thickness of 0.15 mm or less.
Moreover, in order to suppress the deformation of the shape of the semi-finished product, it is the process after slitting to the product width, and no measures are taken for the stainless steel strip for blades after slitting to the product width. It is.
An object of the present invention is to provide a method for producing a stainless steel strip for a knife that can relieve stress remaining in the stainless steel strip for a blade after being slit to the product width and suppress the deformation of the processed semi-finished product. provide.
本発明は上述した課題に鑑みてなされたものである。
すなわち本発明は、刃物用ステンレス帯鋼の製造方法において、仕上冷間圧延を行なって厚さを０．１５ｍｍ以下とした仕上冷間圧延材に対して条取りスリット加工を行い、その後、スリット加工した刃物用ステンレス帯鋼を連続焼鈍炉中を通板させて５００〜６５０℃の温度域の非酸化性ガス雰囲気中で歪取り焼鈍を行って、ビッカース硬さで２９０〜３４０とする刃物用ステンレス帯鋼の製造方法である。
好ましくは、歪取り焼鈍の温度が５５０〜６５０℃であり、歪取り焼鈍後の硬さをビッカース硬さで２９０〜３２０とする刃物用ステンレス帯鋼の製造方法である。
好ましくは、上記の歪取り焼鈍の非酸化性雰囲気は、ＡＸガス、ＮＸガス、Ａｒガス、窒素ガスの何れかである刃物用ステンレス帯鋼の製造方法である。
更に好ましくは、条取りスリット加工は、円形上刃カッターと円形下刃カッターとの協働により行い、それぞれのカッター径は仕上冷間圧延材の板厚に対して１０００倍以上の直径を有する刃物用ステンレス帯鋼の製造方法である。
更に好ましくは、連続焼鈍炉中を通板する刃物用ステンレス帯鋼の炉内張力を１５０Ｎ／ｍｍ２以下の範囲とする刃物用ステンレス帯鋼の製造方法である。
The present invention has been made in view of the above-described problems.
That is, the present invention is a method for manufacturing a stainless steel strip for a blade, and performs finish slit rolling on a finish cold rolled material having a thickness of 0.15 mm or less by finish cold rolling, and then slitting. the cutlery stainless steel strip by performing a stress relief annealing the continuous annealing furnace in a non-oxidizing gas atmosphere at a temperature range of 500 to 650 ° C. by Tsuban, cutlery stainless steel and a Vickers hardness from 290 to 340 It is a manufacturing method of a strip steel.
Preferably, it is a manufacturing method of the stainless steel strip for blades which makes distortion removal annealing temperature 550-650 ° C, and makes hardness after distortion removal annealing 290-320 in Vickers hardness.
Preferably, the non-oxidizing atmosphere of the above-described strain relief annealing is a method for producing a stainless steel strip for blades, which is any one of AX gas, NX gas, Ar gas, and nitrogen gas.
More preferably, the slitting slitting is performed by the cooperation of a circular upper blade cutter and a circular lower blade cutter, and each cutter diameter has a diameter of 1000 times or more with respect to the thickness of the finished cold rolled material. It is a manufacturing method of stainless steel strip.
More preferably, it is the manufacturing method of the stainless steel strip for blades which makes the internal tension of the stainless steel strip for blades passing through the continuous annealing furnace to be in the range of 150 N / mm 2 or less.
本発明の刃物用ステンレス帯鋼の製造方法を適用すれば、製品幅にスリットした後の刃物用ステンレス帯鋼に残留する応力を緩和し、加工を施した半製品の形状変形を抑制することができる。 By applying the method for manufacturing a stainless steel strip for a knife of the present invention, it is possible to relieve stress remaining in the stainless steel strip for a knife after slitting to the product width and to suppress the deformation of the processed semi-finished product. it can.
本発明の重要な特徴は、製品幅にスリットした後の刃物用ステンレス帯鋼に残留する応力を緩和し、加工を施した半製品の形状変形を抑制することができる最適な製造方法にある。
中でも特に、製品幅に条取りスリット後の最適な歪取り焼鈍条件が重要となる。以下に詳しく本発明を説明する。
本発明では、仕上冷間圧延を行なって厚さを０．１５ｍｍ以下とした仕上冷間圧延材を条取りスリット加工を行う。本発明では、製品厚さ、製品幅に調整した刃物用ステンレス帯鋼の素材を対象とする。これは、半製品の形状変形の最大要因が条取りスリット加工時に発生する残留歪にあるためである。
次に、上記のスリット加工した刃物用ステンレス帯鋼を、連続焼鈍炉中を通板させて５００〜６５０℃の温度域の非酸化性ガス雰囲気中で歪取り焼鈍を行う。
本発明で、連続焼鈍炉を用いるのは、単に生産性を考慮しただけのものではなく、連続焼鈍炉を用いることで連続焼鈍炉中を通板する刃物用ステンレス帯鋼に張力を加えられるためである。この張力を例えば炉内張力で１５０Ｎ／ｍｍ２以下の範囲とすると、後述する加熱条件との相乗効果により確実に残留歪を除去することができる。
An important feature of the present invention resides in an optimum manufacturing method that can relieve the stress remaining in the stainless steel strip for blades after being slit to the product width and suppress the shape deformation of the processed semi-finished product.
Among these, the optimum strain relief annealing conditions after the slitting are important for the product width. The present invention is described in detail below.
In the present invention, the finish cold-rolled material having a thickness of 0.15 mm or less by performing finish cold-rolling is subjected to a slitting process. In this invention, the raw material of the stainless steel strip steel for blades adjusted to product thickness and product width is made into object. This is because the largest factor of the shape deformation of the semi-finished product is the residual strain generated during the slitting slit processing.
Next, the above-described slit-processed stainless steel strip for blades is passed through a continuous annealing furnace and subjected to strain relief annealing in a non-oxidizing gas atmosphere in a temperature range of 500 to 650 ° C.
The reason why the continuous annealing furnace is used in the present invention is not only in consideration of productivity, but by using the continuous annealing furnace, tension can be applied to the stainless steel strip for blade passing through the continuous annealing furnace. It is. If this tension is in the range of, for example, 150 N / mm 2 or less in terms of furnace tension, residual strain can be reliably removed by a synergistic effect with heating conditions described later.
そして、本発明では歪取り焼鈍条件は、従来の温度より低目の５００〜６５０℃の温度域と規定した。
これは、スリットした歪がスリットエッジに集中していることから、エッジ部分とその周辺に残留する歪を除去するのに最適な温度であるからである。歪取り焼鈍温度が５００℃未満である場合、スリットしたエッジに残留する歪の除去が不十分となって半製品に加工したときに変形してしまう。そのため、歪取り焼鈍温度の下限を５００℃とした。好ましい下限は５５０℃、より確実な下限は５７５℃である。
一方で歪取り焼鈍温度が６５０℃を超えると、刃物用ステンレス帯鋼の軟化が著しくなる。特にスリットしたエッジ部分は、製品の刃に加工されるため、エッジ部分が過度に加熱されて硬さが低下するのは打抜き加工時にダレが発生し、好ましくない。また、例えば、刃物用ステンレス帯鋼中に微細分散する炭化物が成長したりして、炭化物の形態が変化する危険性もある。そのため、スリットしたエッジに残留する歪を除去でき、且つ、硬さの低下や炭化物の形態の変化を抑制するための上限温度として、６５０℃とした。
但し、上限温度の６５０℃近傍であると、歪取り焼鈍時間が十数秒長くなることで、刃物用ステンレス帯鋼の軟化が顕著になる。そのため、好ましい上限の温度は６１０℃である。
なお、歪取り焼鈍の時間は１５秒〜１２０秒程度で十分である。好ましくは、１５〜６０秒である。後述の実施例で詳しく述べるが、６０秒と１２０秒の歪取り焼鈍後の硬さ、変形量を対比しても、大きな違いは見られない。そのため、経済性を考慮すると、１５〜６０秒の時間が好適である。
Then, stress relief annealing conditions in the present invention was defined as a temperature range of low eye 500 than conventional temperature 650 ° C..
This is because the slitted strain is concentrated on the slit edge, so that the temperature is optimum for removing the strain remaining in the edge portion and the periphery thereof. When the strain relief annealing temperature is less than 500 ° C., the strain remaining on the slit edge is not sufficiently removed, and the product is deformed when processed into a semi-finished product. Therefore, the lower limit of the strain relief annealing temperature is set to 500 ° C. A preferable lower limit is 550 ° C., and a more reliable lower limit is 575 ° C.
On the other hand, if the strain relief annealing temperature exceeds 650 ° C., the softening of the stainless steel strip for blades becomes remarkable. In particular, since the slit edge portion is processed into a blade of the product, it is not preferable that the edge portion is excessively heated and the hardness is lowered because sagging occurs at the time of punching. In addition, for example, there is a risk that carbide that is finely dispersed in the stainless steel strip for blades grows and the morphology of the carbide changes. Therefore, the strain remaining on the slit edge can be removed, and the upper limit temperature for suppressing the decrease in hardness and the change in the form of carbide is set to 650 ° C.
However, when the temperature is in the vicinity of the upper limit temperature of 650 ° C., the strain relief annealing time becomes longer by more than 10 seconds, so that the softening of the stainless steel strip for blades becomes remarkable. Therefore, a preferable upper limit temperature is 610 ° C.
In addition, about 15 seconds to 120 seconds is sufficient as the time for strain relief annealing. Preferably, it is 15 to 60 seconds. As will be described in detail in the examples described later, even if the hardness and deformation amount after 60 seconds and 120 seconds of strain relief annealing are compared, there is no significant difference. Therefore, in consideration of economy, a time of 15 to 60 seconds is preferable.
また、本発明では、歪取り焼鈍後の硬さがビッカース硬さで２９０〜３４０と規定した。このビッカース硬さの範囲内であれば、打抜き加工時のダレの発生をより確実に抑制できる。また、経験上、歪取り焼鈍後の硬さがビッカース硬さで２９０〜３４０であれば、刃物用ステンレス帯鋼中に微細分散する炭化物が成長したりして、炭化物の形態が変化する危険性は低く、また、コイルに巻き易く、高い生産性を得ることができる。
そのため、歪取り焼鈍後の硬さがビッカース硬さで２９０〜３４０とした。好ましくは、２９０〜３２０の範囲であり、この範囲であれば、打抜き加工時のダレの発生を、更に確実に抑制できる。
In the present invention, the hardness after strain relief annealing is defined as 290 to 340 in terms of Vickers hardness. If it is in the range of this Vickers hardness, generation | occurrence | production of the dripping at the time of a punching process can be suppressed more reliably. In addition, experience shows that if the hardness after strain relief annealing is 290 to 340 in terms of Vickers hardness, there is a risk that carbides finely dispersed in the stainless steel strip for blades grow and the shape of the carbides changes. Is easy to wind around the coil, and high productivity can be obtained.
Therefore, the hardness after strain relief annealing was set to 290 to 340 in terms of Vickers hardness. Preferably, it is the range of 290-320, and if it is this range, generation | occurrence | production of the dripping at the time of a punching process can be suppressed further reliably.
そして、本発明では、上記の歪取り焼鈍時に、周囲雰囲気と帯鋼表面の化学反応によって生じる、表面酸化を防止するために、歪取り焼鈍時の雰囲気を非酸化性ガス雰囲気中とする。但し、非酸化性ガスのうち、純水素ガスを高クロム鋼（例えばステンレス鋼）に使用した場合には、水素による還元作用によって不働態膜が破壊され、水素ガス中の微量な不純物（例えば、酸素）と帯鋼表面の化学反応が著しくなるという問題を生じる場合があるため、水素は混合ガスとして用いるのが良い。
そのため、本発明では、７５Ｖｏｌ％水素と２５Ｖｏｌ％窒素との混合ガスのＡＸガスや、窒素を主成分としたＮＸガス、Ａｒガス、窒素ガスを用いるのが良い。
また、本発明では、上述の条取りスリット加工は、円形上刃カッターと円形下刃カッターとの協働により行い、それぞれのカッター径は仕上冷間圧延材の板厚に対して１０００倍以上の直径を有するものを用いるのが良い。
これは、カッター径を大きくするとスリット時の刃物用ステンレス帯鋼スリットエッジ部への歪を軽減でき、上述した歪取り焼鈍の効果をより確実に発揮できるためである。
以上述べた本発明によれば、スリットエッジに集中した歪を確実に除去できることから、スリットした条の両方のスリット面に刃先を形成する刃物の用途に好適である。
And in this invention, in order to prevent the surface oxidation which arises by the chemical reaction of the surrounding atmosphere and the steel strip surface at the time of said strain relief annealing, the atmosphere at the time of strain relief annealing is made into non-oxidizing gas atmosphere. However, among non-oxidizing gases, when pure hydrogen gas is used for high chromium steel (for example, stainless steel), the passive film is destroyed by the reducing action of hydrogen, and a small amount of impurities in the hydrogen gas (for example, Hydrogen may be used as a mixed gas because there may be a problem that the chemical reaction between the oxygen) and the steel strip surface becomes significant.
Therefore, in the present invention, it is preferable to use AX gas, which is a mixed gas of 75 Vol% hydrogen and 25 Vol% nitrogen, or NX gas, Ar gas, or nitrogen gas containing nitrogen as a main component.
Moreover, in the present invention, the above-described slitting slit processing is performed in cooperation with a circular upper blade cutter and a circular lower blade cutter, and the diameter of each cutter is 1000 times or more of the plate thickness of the finished cold rolled material. It is good to use what has a diameter.
This is because, when the cutter diameter is increased, the strain on the stainless steel strip slit edge for cutting can be reduced, and the effect of the above-described strain relief annealing can be more reliably exhibited.
According to the present invention described above, since the strain concentrated on the slit edge can be surely removed, it is suitable for the use of a blade that forms a blade edge on both slit surfaces of the slit.
本発明で対象とする刃物用ステンレス帯鋼の化学組成については特に限定しないが、通常用いられている高Ｃのステンレス鋼を用いるのが良い。以下に示す組成の範囲は質量％である。
例えば、０．３〜１．５％のＣ、１０〜１８％のＣｒ、１％以下のＳｉ、１．５％以下のＭｎを必須として含有し、必要に応じて３％以下のＭｏを含有するＦｅ基の合金である。
Although there is no particular limitation on the chemical composition of the stainless steel strip for blades targeted in the present invention, it is preferable to use a commonly used high-C stainless steel. The range of the composition shown below is mass%.
For example, it contains 0.3 to 1.5% C, 10 to 18% Cr, 1% or less Si, 1.5% or less Mn as an essential component, and 3% or less Mo if necessary. This is an Fe-based alloy.
以下の実施例で本発明を更に詳しく説明する。
大気溶解で作成したマルテンサイト系ステンレス鋼の鋼塊を作製し、鍛造、熱間圧延を行い、焼鈍と冷間圧延を繰返して、仕上冷間圧延を行い、厚さ０．１ｍｍの刃物用ステンレス帯鋼を作製した。化学組成を表１に示す。
The following examples further illustrate the present invention.
A steel ingot made of martensitic stainless steel prepared by melting in the atmosphere is prepared, forged and hot-rolled, repeatedly annealed and cold-rolled, and then cold-rolled into the finish, and 0.1 mm thick stainless steel for blades A strip steel was produced. The chemical composition is shown in Table 1.
作製した厚さ０．１ｍｍの刃物用ステンレス帯鋼を製品幅２３ｍｍに条取りスリット加工した。この時の条取りスリット加工は、円形上刃カッターと円形下刃カッターとの協働により行い、それぞれのカッター径は直径φ１２０ｍｍであった。カッター径は、仕上冷間圧延材の板厚に対して、１０００倍以上の直径を有していた。
次に、スリット加工した刃物用ステンレス帯鋼を連続焼鈍炉中に通板させて５００〜７５０℃の温度にて、非酸化性ガス雰囲気中（ＡＸガス）で歪取り焼鈍を行った。この時、炉内張力は１００Ｎ／ｍｍ２とし、歪取り焼鈍の時間は１５〜１２０秒とした。
The produced stainless steel strip for blades having a thickness of 0.1 mm was striped and slit to a product width of 23 mm. The slitting slit processing at this time was performed in cooperation with a circular upper blade cutter and a circular lower blade cutter, and each cutter diameter was 120 mm in diameter. The cutter diameter had a diameter of 1000 times or more with respect to the thickness of the finished cold rolled material.
Next, the slit-processed stainless steel strip for blades was passed through a continuous annealing furnace and subjected to strain relief annealing in a non-oxidizing gas atmosphere (AX gas) at a temperature of 500 to 750 ° C. At this time, the in-furnace tension was 100 N / mm 2 , and the strain relief annealing time was 15 to 120 seconds.
歪取り焼鈍後の刃物用ステンレス帯鋼を、図１に示す半製品を模擬したエッチング加工を実施し、スリット加工歪の残存によるコーナー部の浮き上がりを確認した。コーナー部の浮き上がりを確認した試験片の寸法は、２３ｍｍ（Ｗ）×２５０（Ｌ）とし、長手方向に２００ｍｍのスリットをエッチングにより形成し、浮き上がり高さを求めた。用いた合金と、歪取り焼鈍の実施有無、歪取り焼鈍の条件、帯鋼の硬さ変化、コーナー部の浮き上がり高さを表２に示す。なお、コーナー部の浮き上がり高さは、０ｍｍ（浮き上がりなし）には◎印を、０ｍｍを超えて１ｍｍまでには○印を、１ｍｍを超えるものには×印を記す。 The stainless steel strip for blades after strain relief annealing was subjected to an etching process simulating the semi-finished product shown in FIG. 1, and the lifting of the corner portion due to the remaining strain of slit machining was confirmed. The dimension of the test piece which confirmed the lift of the corner portion was 23 mm (W) × 250 (L), and a 200 mm slit was formed by etching in the longitudinal direction, and the lift height was obtained. Table 2 shows the alloys used, the presence / absence of strain relief annealing, the conditions for strain relief annealing, the change in hardness of the steel strip , and the raised height of the corner. The raised height of the corner portion is marked with “◎” for 0 mm (no lifting), “◯” for exceeding 0 mm to 1 mm, and “×” for those exceeding 1 mm.
表２に示すとおり、本発明の歪取り焼鈍を実施した刃物用ステンレス帯鋼には、コーナー部の浮き上がりは殆ど見られなかった。但し、歪取り焼鈍温度が５００℃のものでは、１５秒と６０秒のものに１ｍｍ以下の浮き上がりが確認されたことから、５００℃が歪取り焼鈍の下限であることが分る。
また、７００℃で歪取り焼鈍を行なったものは、３０秒の歪取り焼鈍でビッカース硬さが２８０未満に低下したことから、処理時間の調整は若干注意が必要であることが分る。
また、本発明の好ましい温度範囲である５５０〜６５０℃のものでは、１５〜６０秒の処理時間でビッカース硬さ及び変形量が安定して抑制されていることが分る。この５５０〜６５０℃のものでは、処理時間を１２０秒としても硬さの変化が殆ど無いか、或いは、硬さが２８０程度まで低下する結果となったことから、歪取り焼鈍の処理時間は１５〜６０秒の間が最適であることが分る。
また、歪取り焼鈍前後の硬さの変化も殆どなく、歪取り焼鈍が製品幅にスリットした後の刃物用ステンレス帯鋼に残留する応力を緩和できていることも分かる。
As shown in Table 2, in the stainless steel strip for blades subjected to the strain relief annealing of the present invention, almost no lifting of the corner portion was observed. However, when the strain relief annealing temperature is 500 ° C., a lift of 1 mm or less was confirmed at 15 seconds and 60 seconds, and it can be seen that 500 ° C. is the lower limit of the strain relief annealing.
Also, those subjected to stress relief annealing at 700 ° C., since the Vickers hardness in the stress relief annealing of 30 seconds was decreased to less than 280, it can be seen that the adjustment of processing time is somewhat caution.
Moreover, in the thing of 550-650 degreeC which is the preferable temperature range of this invention, it turns out that the Vickers hardness and the deformation | transformation amount are suppressed stably in the processing time of 15-60 seconds. In the case of this 550 to 650 ° C., even if the processing time is 120 seconds, there is almost no change in hardness, or the hardness is reduced to about 280, so the processing time for strain relief annealing is 15 It can be seen that between ˜60 seconds is optimal.
Moreover, there is almost no change in the hardness before and after the strain relief annealing, and it can be seen that the stress remaining in the stainless steel strip for blades after the strain relief annealing is slit to the product width can be alleviated.
本発明は刃物用ステンレス帯鋼の残留歪を低減することで、例えば、打抜き等の加工後の製品に高い加工精度を有することが不可欠な用途に適用できる。また、歪取り焼鈍前後の硬さ変化が非常に小さいため、例えば、打抜き加工を施す用途に最適である。 The present invention can be applied to a use in which it is indispensable to have high processing accuracy in a product after processing such as punching, for example, by reducing the residual strain of the stainless steel strip for blades. In addition, since the change in hardness before and after the strain relief annealing is very small, it is most suitable for, for example, a punching process.
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