JP2005113203A - Martensitic stainless steel for door member, and its production method - Google Patents
Martensitic stainless steel for door member, and its production method Download PDFInfo
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- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract description 12
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 26
- 239000010959 steel Substances 0.000 claims abstract description 26
- 238000010791 quenching Methods 0.000 claims abstract description 15
- 230000000171 quenching effect Effects 0.000 claims abstract description 15
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 12
- 239000000203 mixture Substances 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 238000005496 tempering Methods 0.000 claims description 11
- 238000005520 cutting process Methods 0.000 abstract description 6
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract 1
- 229910052751 metal Inorganic materials 0.000 abstract 1
- 239000002184 metal Substances 0.000 abstract 1
- 150000002739 metals Chemical class 0.000 abstract 1
- 230000035515 penetration Effects 0.000 description 13
- 239000000463 material Substances 0.000 description 12
- 238000012360 testing method Methods 0.000 description 9
- 238000001816 cooling Methods 0.000 description 7
- 238000002791 soaking Methods 0.000 description 5
- 229910001220 stainless steel Inorganic materials 0.000 description 5
- 239000010935 stainless steel Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910000926 A-3 tool steel Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000005553 drilling Methods 0.000 description 3
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、住居等のドア部材に用いられるマルテンサイト系ステンレス鋼に関する。 The present invention relates to a martensitic stainless steel used for a door member such as a residence.
マンション等の住居のドア部材には、意匠性の他に耐食性をも要求されるため、化粧鋼板に代わってオーステナイト系ステンレス鋼板が使用されようとしている。また、特許文献１では、ＳＵＳ３０４等のオーステナイト系ステンレス鋼板を使用したドア部材の問題点を改善するために、３０質量％以上のＣｒと２質量％以上のＭｏを含有したステンレス鋼板を使用することが提案されている。
また、住居用のドア部材ではないが、溶断を防ぐための対策を講じたドア構造が特許文献２で提案されている。
Since a door member of a residence such as an apartment is required to have corrosion resistance in addition to design, an austenitic stainless steel plate is about to be used instead of a decorative steel plate. Moreover, in patent document 1, in order to improve the problem of the door member which uses austenitic stainless steel plates, such as SUS304, use the stainless steel plate containing 30 mass% or more of Cr and 2 mass% or more of Mo. Has been proposed.
Moreover, although it is not a door member for residences, the door structure which took the measure for preventing a fusing is proposed by patent document 2. FIG.
ところで、近年、住居のドアの鍵穴近傍にドリルで穴を開け、手で鍵を開けて住居内に侵入する手口の盗難が急増している。
ＳＵＳ３０４のステンレス鋼板や特許文献１で提案された高Ｃｒステンレス鋼板は、硬さがさほど高くないので、ドリルにより容易に穴あけを行うことができる。したがって上記のような盗難対策には効果的ではない。特許文献２で提案された対策は、現金自動取引装置（ＡＴＭ）等、厳重な盗難対策を必要とする扉等に講じられるものであるから、この対策を一般の住居に適用することは、コストの点からも有効ではない。
本発明は、このような問題を解消すべく案出されたものであり、住居のドア部材として、ドリルでの切削が困難なほどに硬いマルテンサイト系ステンレス鋼を提供することを目的とする。
By the way, in recent years, there has been a rapid increase in theft of tricks that are drilled in the vicinity of the keyholes in the doors of houses and opened by hand to enter the house.
Since the stainless steel plate of SUS304 and the high Cr stainless steel plate proposed in Patent Document 1 are not so hard, they can be easily drilled with a drill. Therefore, it is not effective as a countermeasure against theft as described above. Since the countermeasure proposed in Patent Document 2 is applied to doors that require strict countermeasures against theft such as an automatic teller machine (ATM), it is costly to apply this countermeasure to a general residence. From the point of view, it is not effective.
The present invention has been devised to solve such a problem, and an object of the present invention is to provide martensitic stainless steel that is hard enough to be cut with a drill as a door member of a house.
本発明のドア部材用マルテンサイト系ステンレス鋼は、その目的を達成するため、Ｃ：０．０５〜１．２質量％，Ｃｒ：８〜１８質量％，Ｓｉ：１．０質量％以下，Ｍｎ：１．０質量％以下を含み、残部が実質的にＦｅからなる組成を有するとともに、マルテンサイト組織を呈し、かつビッカース硬度で５００ＨＶ以上の硬さを有することを特徴とする。
この鋼は、さらに、Ｔｉ，Ｎｂ，Ｖ，Ｗ及びＭｏの少なくとも１種以上を合計で０．０５〜１．０質量％を含むものでもよい。
上記組成を有する鋼を、１０００〜１１５０℃で保持した後、焼入れ処理することにより、マルテンサイト組織を呈し、かつビッカース硬度で５００ＨＶ以上の硬さを有するものが得られる。
焼入れ後、さらに４００℃以下の温度で焼戻し処理すると、靭性をも有するものが得られる。
In order to achieve the object, the martensitic stainless steel for door members of the present invention has C: 0.05 to 1.2% by mass, Cr: 8 to 18% by mass, Si: 1.0% by mass or less, Mn : 1.0% by mass or less, with the balance being substantially composed of Fe, having a martensitic structure, and having a Vickers hardness of 500 HV or more.
This steel may further contain 0.05 to 1.0% by mass in total of at least one of Ti, Nb, V, W and Mo.
By holding the steel having the above composition at 1000 to 1150 ° C. and then quenching it, a steel having a martensite structure and having a Vickers hardness of 500 HV or more is obtained.
When tempering is further performed at a temperature of 400 ° C. or lower after quenching, a product having toughness can be obtained.
本発明により、ドリルにより穴を開けようとしても開穴に時間を要し、場合によってはドリルそのものが破損されるほどの硬質なマルテンサイト系ステンレス鋼が得られる。したがって当該ステンレス鋼鋼を、ドア部材の表板や裏板に用いることにより、あるいは鍵穴周辺の表板と裏板間に介在させることにより、鍵穴近傍のドア部材をドリルで穴開けすることは困難となる。すなわち、本発明により、防犯効果に優れるドア部材用素材を、比較的低コストで提供することができる。 According to the present invention, it is possible to obtain martensitic stainless steel that is so hard that it takes time to open a hole with a drill, and the drill itself may be damaged in some cases. Therefore, it is difficult to drill the door member in the vicinity of the keyhole by using the stainless steel for the front plate or the back plate of the door member or by interposing between the front plate and the back plate around the key hole. It becomes. That is, according to the present invention, it is possible to provide a door member material having an excellent crime prevention effect at a relatively low cost.
本発明者等は、課題解決のため鋭意検討した結果、マルテンサイト系ステンレス鋼の硬さを調整することにより、ドリルでの切削が困難な材料を提供できることを見出した。
すなわち、本発明者等は、成分、製造条件を種々変動させることにより硬さを変えた５．０ｍｍのステンレス鋼板を実験室的に作製し、それぞれの鋼板にドリルで穴を開け、穴が貫通するまでの時間を調査した。
その結果、材料の硬さが５００ＨＶを超えるとドリルで穴を貫通させるまでに要する時間（以下、「ドリル貫通時間」という。）が急激に増加することが判明した。
As a result of intensive studies for solving the problems, the present inventors have found that a material that is difficult to cut with a drill can be provided by adjusting the hardness of martensitic stainless steel.
In other words, the inventors made 5.0 mm stainless steel plates with varying hardness by varying the components and manufacturing conditions in the laboratory, drilled holes in each steel plate, and the holes penetrated. Investigate the time to do.
As a result, it was found that when the hardness of the material exceeds 500 HV, the time required to penetrate the hole with a drill (hereinafter referred to as “drill penetration time”) increases rapidly.
図１に、材料の硬さとドリル貫通時間の関係を示す。ドリル貫通時間は、硬さの増加にともない緩やかに増加し、硬さが５００ＨＶを超えると急増することがわかる。
なお、硬さは、ビッカース硬度計を用いて荷重９８Ｎで測定したものである。また、ドリル試験の条件は表１に示す通りであり、用いたドリルは一般的なＪＩＳ Ｂ４３０１に規定されているＨＳＳストレートドリルである。
FIG. 1 shows the relationship between material hardness and drill penetration time. It can be seen that the drill penetration time increases gradually with increasing hardness, and increases rapidly when the hardness exceeds 500 HV.
The hardness was measured with a load of 98 N using a Vickers hardness tester. The conditions of the drill test are as shown in Table 1, and the drill used is an HSS straight drill defined in general JIS B4301.
上記ドリル穿穴試験で用いたＨＳＳドリルの硬さは表面の刃の部分で８２０ＨＶ、断面で５８０ＨＶである。図１の結果とあわせて考えると、ドリルでの切削は、材料の硬さがドリル断面の硬さに近づくと困難になることがわかる。ドリルでの切削では、ドリル刃を被切削材に回転させながら押し付けることにより、刃によって被切削材を削り取っていく作業であるから、当然ながら、切削のためにはドリル刃は被切削材よりも硬くなくてはならない。逆にいえば、被切削材がドリル刃と同等以上の硬さを有する時には切削は困難になる。 The hardness of the HSS drill used in the drill drilling test is 820 HV for the surface blade portion and 580 HV for the cross section. Considering together with the results of FIG. 1, it can be seen that cutting with a drill becomes difficult when the hardness of the material approaches the hardness of the drill cross section. In cutting with a drill, the drill blade is pressed against the workpiece while rotating it, and the workpiece is scraped off by the blade. Must be hard. In other words, cutting becomes difficult when the material to be cut has a hardness equal to or higher than that of the drill blade.
この点をふまえると、被切削材の硬さが５００ＨＶでドリル貫通時間が急増した理由は以下のように考えられる。
被切削材が硬いとドリル刃が材料の凝着摩耗等により損傷し、内部の軟らかい箇所が表面に現れる。ドリル内部の硬さは上述したように５８０ＨＶであるから、被切削材の硬さがそれに近い５００ＨＶ以上であると、切削が困難となってドリル貫通時間も急増する。また、ドリル貫通試験を行った後のドリルの刃先を観察してみた。ＨＶ１６８の鋼板では４秒で貫通でき、貫通させた後のドリルもわずかに摩耗している程度で、外観的にはほとんど変形を受けていない。ＨＶ５７２の鋼板では、貫通までの１５３秒を要し、貫通させた後のドリルは、摩耗も激しく、部分的に破損していた。さらに、ＨＶ６２９の鋼板では、ドリルを貫通させることはできず、ドリル表面を見ると破損が激しかった。
Considering this point, the reason why the drill penetration time increased rapidly when the hardness of the work material was 500 HV is considered as follows.
If the material to be cut is hard, the drill blade is damaged due to adhesive wear of the material, and a soft portion inside appears on the surface. Since the hardness inside the drill is 580 HV as described above, if the hardness of the material to be cut is 500 HV or higher, the cutting becomes difficult and the drill penetration time increases rapidly. In addition, the drill edge after the drill penetration test was observed. The HV168 steel plate can be penetrated in 4 seconds, and the drill after being penetrated is slightly worn, and is hardly deformed in appearance. The HV572 steel plate required 153 seconds to penetrate, and the drill after penetration was severely worn and partially damaged. Furthermore, in the HV629 steel plate, the drill could not be penetrated, and the drill surface was severely damaged.
一般的なＨＳＳストレートドリルの刃の硬さは表面で７７２ＨＶ以上とＪＩＳ Ｂ４３０１で規定されているが、その断面硬さはいずれも５８０ＨＶ程度である。したがって、上記の結果から考えると、ドリルでの切削を困難にするためには、被切削材の硬さは５００ＨＶ以上にする必要がある。そこで、本発明では、ドア部材用マルテンサイト系ステンレス鋼の硬さを５００Ｈ以上に規定した。 The hardness of a blade of a general HSS straight drill is 772 HV or more on the surface and specified in JIS B4301, but the cross-sectional hardness of each is about 580 HV. Therefore, considering the above results, the hardness of the workpiece needs to be 500 HV or higher in order to make cutting with a drill difficult. Therefore, in the present invention, the hardness of the martensitic stainless steel for door members is regulated to 500H or more.
以下に、本発明ドア部材用鋼の成分組成、組織、その製造条件等について詳しく説明する。
Ｃ：０．０５〜１．２質量％
Ｃは、焼入れ処理によりマルテンサイト組織を得るために０．０５質量％以上含有させる必要がある。しかし、Ｃ含有量が１．２質量％を超えると、共晶炭化物が多量に析出し、熱間加工性を低下させる。したがって、Ｃ含有量は０．０５〜１．２質量％の範囲とする。
Below, the component composition, structure | tissue, its manufacturing conditions, etc. of steel for this invention door members are demonstrated in detail.
C: 0.05-1.2 mass%
C needs to be contained in an amount of 0.05% by mass or more in order to obtain a martensite structure by quenching treatment. However, if the C content exceeds 1.2% by mass, a large amount of eutectic carbide precipitates and the hot workability is lowered. Therefore, the C content is in the range of 0.05 to 1.2% by mass.
Ｃｒ：８〜１８質量％
Ｃｒは、耐食性を付与するために必要な成分である。本発明材が用いられる環境を考慮すると、８質量％以上含まれることが必要である。しかし、過剰に含ませることは製造コストの上昇を招くので上限は１８質量％とした。
Ｓｉ：１．０質量％以下，Ｍｎ：１．０質量％以下
Ｓｉ，Ｍｎは鋼の脱酸に必要な成分である。しかし、過剰の添加は、その効果を飽和させるばかりでなく、製造コストを上昇させることにもなる。したがって、その上限はそれぞれ１．０質量％とした。
Cr: 8 to 18% by mass
Cr is a component necessary for imparting corrosion resistance. Considering the environment in which the material of the present invention is used, it is necessary to be contained by 8% by mass or more. However, excessive inclusion causes an increase in manufacturing cost, so the upper limit was made 18% by mass.
Si: 1.0 mass% or less, Mn: 1.0 mass% or less Si and Mn are components necessary for deoxidation of steel. However, excessive addition not only saturates the effect, but also increases the manufacturing cost. Therefore, the upper limit was set to 1.0% by mass.
Ｔｉ，Ｎｂ，Ｖ，Ｗ及びＭｏの少なくとも１種以上を合計で０．０５〜１．０質量％
Ｔｉ，Ｎｂ，Ｖ，ＷあるいはＭｏは、その炭化物を鋼の基地中に分散させることにより硬さを増加させる作用を有しているので、必要に応じて添加される。ただし、炭化物の分散量が少ないとその効果が低いため、それぞれ単独で、あるいは組み合わせで、０．０５質量％以上添加することが好ましい。しかし、これらの成分を過剰に添加すると、金属間化合物の生成による靭性の低下を招くため、その上限は１．０質量％とした。
0.05 to 1.0% by mass in total of at least one of Ti, Nb, V, W and Mo
Ti, Nb, V, W, or Mo has an effect of increasing hardness by dispersing the carbide in the steel matrix, and is added as necessary. However, since the effect is low when the amount of carbide dispersion is small, it is preferable to add 0.05% by mass or more individually or in combination. However, if these components are added excessively, the toughness is reduced due to the formation of intermetallic compounds, so the upper limit was made 1.0 mass%.
マルテンサイト組織
マルテンサイト組織は、高密度の転位を内蔵するとともに過飽和の炭素を固溶しているため、高い硬さを有している。本発明で規定される成分範囲の鋼を焼入れ処理することにより、マルテンサイト組織を得ることができる。他のフェライト組織やオーステナイト組織では焼入れ処理により５００ＨＶ以上の硬さを得ることは困難であることから、組織はマルテンサイト組織に限定した。
Martensitic structure The martensitic structure has high hardness because it contains high-density dislocations and has a solid solution of supersaturated carbon. A martensitic structure can be obtained by quenching the steel in the component range defined in the present invention. In other ferrite structures and austenite structures, it is difficult to obtain a hardness of 500 HV or higher by quenching, so the structure is limited to a martensite structure.
焼入れ温度：１０００〜１１５０℃
焼入れ処理とは、鋼を加熱して高温でオーステナイト組織にした後、冷却して室温でマルテンサイト組織を得るために行うものである。本発明で規定する範囲の成分組成を有する鋼は、１０００〜１１５０℃の範囲でオーステナイト組織となる。そこで、焼入れ温度の範囲は１０００〜１１５０℃とした。
焼戻し温度：４００℃以下
焼戻しとは、焼入れ処理で得たマルテンサイト組織をＡｃ１点以下の温度に加熱し、冷却する処理のことである。この処理は、固溶している炭素を炭化物として析出させるとともに、基地組織を回復させて靭性を付与するために、必要に応じて行うものである。
４００℃を超える温度で焼戻し処理を行うと、炭化物の析出と回復が進行し、硬さが５００ＨＶ以下となってしまう。そこで、焼戻しの温度範囲は４００℃以下とした。
Quenching temperature: 1000-1150 ° C
The quenching treatment is performed in order to obtain a martensite structure at room temperature after heating the steel to form an austenite structure at a high temperature. Steel having a component composition in the range specified in the present invention has an austenite structure in the range of 1000 to 1150 ° C. Therefore, the range of quenching temperature was set to 1000 to 1150 ° C.
Tempering temperature: 400 ° C. or lower Tempering is a process of heating and cooling the martensite structure obtained by quenching to a temperature of Ac1 or lower. This treatment is performed as necessary in order to precipitate solid carbon as carbides and to recover the base structure and impart toughness.
When the tempering process is performed at a temperature exceeding 400 ° C., the precipitation and recovery of carbide proceeds, and the hardness becomes 500 HV or less. Therefore, the temperature range for tempering was set to 400 ° C. or less.
表２に示す成分組成を有する鋼３０ｇを真空溶解炉にて溶解し、各鋼とも熱間圧延を経て板厚５．０ｍｍの熱延板を製造した。なお、表２において、供試鋼Ａ１〜Ａ３が本発明で規定する成分組成を有する発明対象鋼，Ｂ１，Ｂ２が比較鋼である。
各熱延版を、９００℃あるいは１０５０℃で１０分間均熱後に水冷した。さらに、１０５０℃で１０分間均熱後水冷した供試鋼Ａ１−Ａ３については、焼入れ処理後、２５０℃×１分保持後空冷、あるいは４５０℃×１分保持後空冷の条件で焼戻し処理を施した。
30 g of steel having the composition shown in Table 2 was melted in a vacuum melting furnace, and each steel was hot-rolled to produce a hot rolled sheet having a thickness of 5.0 mm. In Table 2, the steels under test A1 to A3 have the component composition defined in the present invention, and B1 and B2 are comparative steels.
Each hot rolled plate was water-cooled after soaking at 900 ° C. or 1050 ° C. for 10 minutes. Further, the test steel A1-A3, which was soaked at 1050 ° C. for 10 minutes and then water-cooled, was subjected to tempering treatment after quenching under the conditions of air cooling after holding at 250 ° C. × 1 minute or air cooling after holding at 450 ° C. × 1 minute. did.
焼入れ処理、あるいは焼入れ処理と焼戻し処理を施した各熱延板について、硬さ試験，光学顕微鏡観察及びドリル穿穴試験を行った。
なお、硬さは、ビッカース硬度計を用いて荷重９８Ｎで測定し、５個の測定点の平均値で評価した。光学顕微鏡観察は、圧延方向に垂直な断面をバフ研磨後、混酸でエッチングした試料で組織を確認した。またドリル穿穴試験は、前記表１で示す条件にて穿穴を行い、ドリル貫通時間で評価した。
その試験結果を表３に示す。
A hardness test, an optical microscope observation, and a drill hole test were performed on each hot-rolled sheet subjected to quenching treatment or quenching treatment and tempering treatment.
The hardness was measured with a load of 98 N using a Vickers hardness meter, and the average value of five measurement points was evaluated. Optical microscope observation confirmed the structure | tissue with the sample which etched the cross section perpendicular | vertical to a rolling direction with the mixed acid after buffing. In the drill drilling test, drilling was performed under the conditions shown in Table 1, and the drill penetration time was evaluated.
The test results are shown in Table 3.
１０５０℃で１０分間均熱後に水冷処理を施したＡ１〜Ａ３鋼、あるいは１０５０℃で１０分間均熱後に水冷処理を施し、さらにその後２５０℃の焼戻し処理を施したＡ１〜Ａ３鋼は、成分組成，焼入れ温度，焼戻し温度，組織，硬さともに本発明で規定する範囲にあり、優れた耐ドリル貫通性を示していた。
これに対して、９００℃で１０分間均熱後に水冷処理を施したＡ１〜Ａ３鋼、あるいは１０５０℃で１０分間均熱後に水冷処理を施し、さらにその後４５０℃の焼戻し処理を施したＡ１〜Ａ３鋼は、硬さが低下し本発明で規定する範囲外であるために、耐ドリル貫通性は不良であった。
また、比較鋼であるＢ−１鋼は、Ｃ含有量が少ないために焼入れ処理を施してもマルテンサイト組織にならず、所望の硬さが得られないので、ドリル貫通時間は著しく短かった。同じく比較例であるＢ−２鋼は、オーステナイト組織を呈する鋼であるために、所望の硬さが得られず、ドリル貫通時間は著しく短かった。
A1 to A3 steel subjected to water cooling treatment after soaking at 1050 ° C. for 10 minutes, or A1 to A3 steel subjected to water cooling treatment after soaking at 1050 ° C. for 10 minutes and further subjected to tempering treatment at 250 ° C. The quenching temperature, tempering temperature, structure, and hardness were within the ranges specified by the present invention, and excellent drill penetration resistance was exhibited.
On the other hand, A1 to A3 steel subjected to water cooling treatment after soaking at 900 ° C. for 10 minutes, or A1 to A3 subjected to water cooling treatment after soaking at 1050 ° C. for 10 minutes and further subjected to tempering treatment at 450 ° C. Since the steel has a reduced hardness and is outside the range defined in the present invention, the drill penetration resistance was poor.
Further, B-1 steel, which is a comparative steel, has a low C content, so even if it is quenched, it does not have a martensite structure, and the desired hardness cannot be obtained, so that the drill penetration time is extremely short. Similarly, B-2 steel, which is a comparative example, is a steel exhibiting an austenite structure, so that the desired hardness was not obtained and the drill penetration time was extremely short.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008231517A (en) * | 2007-03-20 | 2008-10-02 | Nisshin Steel Co Ltd | Stainless steel material for cutting tool and its manufacturing method |
| KR102030804B1 (en) * | 2019-07-10 | 2019-10-10 | (주)우석엔지니어링 | Ax and method for manufacturing the same |
| KR20200083006A (en) * | 2018-12-31 | 2020-07-08 | 고려전통기술 주식회사 | Method for manufacturing knife |
| JP7404792B2 (en) | 2018-12-04 | 2023-12-26 | 株式会社プロテリアル | Martensitic stainless steel parts and their manufacturing method |
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2003
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008231517A (en) * | 2007-03-20 | 2008-10-02 | Nisshin Steel Co Ltd | Stainless steel material for cutting tool and its manufacturing method |
| JP7404792B2 (en) | 2018-12-04 | 2023-12-26 | 株式会社プロテリアル | Martensitic stainless steel parts and their manufacturing method |
| KR20200083006A (en) * | 2018-12-31 | 2020-07-08 | 고려전통기술 주식회사 | Method for manufacturing knife |
| KR102136827B1 (en) | 2018-12-31 | 2020-07-22 | 고려전통기술 주식회사 | Method for manufacturing knife |
| KR102030804B1 (en) * | 2019-07-10 | 2019-10-10 | (주)우석엔지니어링 | Ax and method for manufacturing the same |
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