JPH03180447A - Drill steel - Google Patents
Drill steelInfo
- Publication number
- JPH03180447A JPH03180447A JP1317685A JP31768589A JPH03180447A JP H03180447 A JPH03180447 A JP H03180447A JP 1317685 A JP1317685 A JP 1317685A JP 31768589 A JP31768589 A JP 31768589A JP H03180447 A JPH03180447 A JP H03180447A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- toughness
- wear resistance
- carbides
- drill
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 32
- 239000010959 steel Substances 0.000 title claims abstract description 32
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 238000009628 steelmaking Methods 0.000 claims abstract description 3
- 229910052799 carbon Inorganic materials 0.000 claims abstract 3
- 238000005553 drilling Methods 0.000 claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 150000001247 metal acetylides Chemical class 0.000 abstract description 11
- 239000000463 material Substances 0.000 abstract description 7
- 229910000997 High-speed steel Inorganic materials 0.000 abstract description 6
- 238000003754 machining Methods 0.000 abstract description 4
- 239000010935 stainless steel Substances 0.000 abstract description 4
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 4
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 238000005520 cutting process Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 238000010791 quenching Methods 0.000 description 9
- 230000000171 quenching effect Effects 0.000 description 9
- 238000005496 tempering Methods 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000010730 cutting oil Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 230000009291 secondary effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Drilling Tools (AREA)
Abstract
Description
[産業上の利用分野J
本発明は、主としてステンレス鋼などの・難加工材の穴
あけ加工に好適なドリル用鋼に関する。
[従来の技術]
ドリル用鋼には5KH51が汎用されているが、被削材
がステンレス鋼のような粘くかつ加工硬化の大なる鋼の
加工では、切屑の破砕性か悪く、切削温度のL昇と切削
抵抗の増大をもたらし著しく加工寿命を劣化させる。こ
のような難加工材の切削に用いられろドリル用鋼には従
来JIS 5KH56または5KH59等のCo系高速
度鋼が選択されている。[Industrial Field of Application J] The present invention relates to a drill steel suitable for drilling in materials that are difficult to machine, such as mainly stainless steel. [Prior art] 5KH51 is commonly used as steel for drills, but when machining sticky and highly work-hardened work materials such as stainless steel, it has poor chip crushability and low cutting temperatures. This causes an increase in L height and cutting resistance, which significantly deteriorates machining life. Conventionally, Co-based high-speed steel such as JIS 5KH56 or 5KH59 has been selected as the drill steel used for cutting such difficult-to-process materials.
【発明が解決しようとする問題点J
ドリル寿命は、刃先の摩耗、チッピングおよび折損等が
その原因となるが、加工ll緘によってもその寿命は変
わる。比較的剛性の小さいボール盤では、ドリルのフレ
が大きく、従来のCo系高速度鋼を使ったドリルでも、
その寿命に限界が生じている。ドリル刃先の生じるチッ
ピングJ、i、び摩耗は、ドリル用鋼の耐摩耗性、靭性
&と影響され、これらIIM的性質の向上が不可欠とな
る。
本発明は、従来の5KH56、5KH59に代表される
Co系高速度鋼よりも耐摩耗性および靭性を向上させた
ドリル用鋼に関−する。
E問題点を解決するための手段及び作用J一般に高速度
鋼の耐摩耗性は基地の硬さと鋼中に存在する炭化物の種
類と量に依存する。特に焼入れによって残留する硬質の
肛炭化物の影響が大きく、それは主成分のVWによって
特に決定される。ところがMC炭化物の一部は焼入時に
固溶して基地に分配されるので、実際に多量の&IC炭
化物を形成させるには、■遣を増やすと同時にCIをも
増やす必要があった。このような手段は、 MC炭化物
の凝集と粗大化を招いて焼入時に多量のMC炭化物を残
留させる反面、基地のC,VNkを減少させるので焼も
どしによる二次硬化が十分に得られず基地の硬さを減す
る結果、耐摩耗性の向上と靭性向上に限界が生じる。本
発明者等は、熱処理後の基地硬さと残留炭化物のコント
ロールの手段として、 Nbを添加させることにより安
定な未溶解のNbC炭化物を形成させ、残留炭化物凝の
コントロールを容易にすると同時にNb/V比を適正範
囲にとどめることにより基地へのC1■の固溶を容易に
した結果、耐摩耗性と靭性の向ヒか計れることを見いだ
した。
すなわち本発明鋼は、’ILKt%で、C:0.70〜
1.20%、Si : 0.30〜1.50%、 14
n: 1.0%以下、Cr: 3.0〜6.0%、Mo
: 5.0〜10.0%、W + 1.0〜9.0%、
■二〇、5〜!、25%、Nb:0.5〜1.0%、(
:o:5.0〜12.[1%、残部が鉄および製鋼上不
可避の不純物を含有する鋼であって、Nb/V比が0.
8〜1.5を満たすドリル用鋼である。
次に本発明鋼を構成する合金元素の限定理由についで以
下に述べる。
C: Cr、 Mo、 W、 V、 Nb7.、xどの
炭化物形成元素と−zsca 、 54sC、MC型炭
化物を形成し、一部は、基地に固溶する。 ドリル用鋼
の必要な基地強化とNbC形成に必要なC徹とし−C最
低0.7%以上を含有させる。1.2%以上の過剰のC
は、加工性と靭性を阻害するので上限を1.2%とする
。
Si:製鋼上脱酸剤として効果を持つと同時に強度と耐
軟化性を改善するが多量の添加は、熱間および冷間の加
工性を害するのでその範囲を0.3〜1.5%とする。
Mn:Siと同様に5J14上脱酸剤として添加するが
耐摩耗性と靭性の改善には影響するところが少ないので
、その範囲を1.0%以下とする。
C「:主としてL3Cs炭化物を形成し、焼入時に殆ど
基地に固溶して、基地を強化することにより高温強度を
高める。また、Crは、焼入性を高める作用がある。少
なくと433%以上は必要で、6%以上では特性上のメ
リット、経済性のメリットがでないので、その範囲を3
〜6%とする。
Mo:焼ちどし軟化抵抗を高めるととちに、二次効果を
大ならしめることにより、耐摩耗性を付与する6 ドリ
ル用鋼として必要な硬さを得るために5.0%以上を含
有させるが、l010%以上では棒状の粗大M、C炭化
物を形成し、焼入性を劣化させるので最適成分範囲を5
.0〜10.0%とする。
W : Moと同様に焼もどし硬化能と軟化抵抗を高め
、耐熱性を付与する。同時に、主として&+6C型炭化
物を形成し耐摩耗性をも与える。1%以下ではその効果
が少なく、9%以上では熱間加工性を害するとともにM
、C型炭化物の粗大化を招き、焼入性5靭性を害するの
でその範囲を1.0〜9.0%とする。
V:高速度鋼では強力jl炭化物形成元素で、■添加機
が多い場合は、焼入時に未溶解の残留炭化物として残る
量が多くなり、これが耐摩耗性に寄与する。またVは、
焼ちどし2次硬化に寄与する6本発明鋼のVlは、焼入
後に未溶解の残留炭化物を殆ど残さない範囲、すなわち
焼もどし2次硬化に必要な範囲にとどめる。VO15%
以下では、焼もどしによる炭化物析出量が少ないためド
リル用鋼に必要なIIR(:65以上の硬さが得られず
。
1.25%以上では、上記未溶解の残留粗大炭化物を形
成し、研削性の阻害要因となるので、その範囲を0.5
〜1.25%とする。
Nb:Nbの大部分は、安定で硬質のNbC炭化物を形
成し焼入加熱において基地中に溶解せず本発明の目的の
一つとする耐摩耗性を向上させる。
方、微細な分布は結晶粒の粗大化抑止効果を6つので靭
性をも改善する。0.3%以下では、その効果は少7f
<、1.0%以−ヒでは焼入性および到達硬さを下げる
と同時に、 NbC炭化物の粗大化を来すので、その範
囲を0.3〜1.0%とする。
Nb/V比が0.8〜1.5%で最も良好な耐摩耗性と
靭性の関係がI与られることを見いだした0本発明鋼の
成分範囲にあって、 Nb/V比が、0.8未満では、
第2表の実施例、第3表の効果に示すごとく靭性及び切
削耐久寿命を減殺し、またNb/V比が1.5を超えて
多機に添加すると熱処理硬さが不足とjzり耐摩耗性や
切削耐久寿命が低下するためNb/V比は0.8〜1.
5の範囲に限定した。
Co:基地に全壁固溶し、基地強化と軟化抵抗を高める
作用があり、工具の温度上界に対して抵抗性をもつ、上
記作用を有効にするためには、少くと65.0%添加す
る必要がある。 Coが多い程、その効果は著しいが1
2.0%以上の添加は、熱間および冷間の伸びが小さく
なり加工性を害すると同時に高価なため経済性をそこな
うので12.0%以下とする。
【実施例】
第1表は真空溶解炉50Kg鋼塊を溶製し、鍛造。
圧延後φ20丸鋼とした本発明鋼および比鮫鋼の化学成
分を示す。
第2表は、φ20供試鋼を焼入温度1200℃、焼ちと
し560 ’Cx l H3回の熱処理を行った時の焼
入焼もどし峡さ、オーステナイト結晶粒度、3点曲げ荷
重による抗折力、入超式摩耗試験機で相手材S(1g
415 、摩擦速度0.24m/sec 、 F’を擦
距離400m、最終荷重12.6にgの試験条件のとき
の比摩耗量の結果を示す。
第2表に示すように、本発明鋼は、ドリル用鋼に必要な
HRC65以上の硬さを得るとともに比較鋼よりも優れ
た靭性と耐摩耗性を有している。
第3表は、供試鋼よりφ6ストレートドリルを製作し、
ボール盤によって穴あけ加工を行った時の切削耐久#命
の結東を示す、切削条件は、回転数745r、p、m、
切削速度14m/win 、送り0.15m*/「f!
V 、穴深さ20m5+貫通穴とし、水溶性の切削油を
使用した。被削材は、5tlS304. HB185
ヲ用イタ。
第3表
[効果1
本発明鋼によれば、ドリル用鋼として必要な耐摩耗性と
靭性の向上を得ることが出来るので、ステンレス鋼等の
難加工材の切削耐久々命を大幅に改善することができる
。[Problem to be Solved by the Invention J] The lifespan of a drill is caused by wear, chipping, breakage, etc. of the cutting edge, but the lifespan also changes depending on the machining process. Drilling machines with relatively low rigidity have large drill runout, and even drills using conventional Co-based high-speed steel,
There is a limit to its lifespan. The chipping and wear of the drill cutting edge are affected by the wear resistance and toughness of the drill steel, and it is essential to improve these IIM properties. The present invention relates to a drill steel that has improved wear resistance and toughness over conventional Co-based high-speed steels such as 5KH56 and 5KH59. EMeans and actions for solving the problemJ Generally, the wear resistance of high-speed steel depends on the hardness of the matrix and the type and amount of carbides present in the steel. In particular, the influence of hard carbide remaining after quenching is large, and it is particularly determined by the main component VW. However, some of the MC carbides are dissolved in the solid solution during quenching and distributed to the matrix, so in order to actually form a large amount of &IC carbides, it was necessary to increase the amount of ■ and at the same time increase the CI. Such a method causes the agglomeration and coarsening of MC carbides, leaving a large amount of MC carbides during quenching, but on the other hand, it reduces the C and VNk of the matrix, making it impossible to obtain sufficient secondary hardening through tempering. As a result of reducing the hardness, there is a limit to the improvement of wear resistance and toughness. The present inventors added Nb to form stable undissolved NbC carbide as a means of controlling the base hardness and residual carbide after heat treatment, and at the same time, the Nb/V It was discovered that by keeping the ratio within an appropriate range, it was possible to improve the wear resistance and toughness by facilitating the solid solution of C1 into the matrix. That is, the steel of the present invention has C: 0.70 to 0.70 in ILKt%.
1.20%, Si: 0.30-1.50%, 14
n: 1.0% or less, Cr: 3.0-6.0%, Mo
: 5.0~10.0%, W+1.0~9.0%,
■20, 5~! , 25%, Nb: 0.5-1.0%, (
:o:5.0-12. [1%, the balance is steel containing iron and impurities inevitable in steelmaking, and the Nb/V ratio is 0.
It is steel for drills that satisfies 8 to 1.5. Next, the reasons for limiting the alloy elements constituting the steel of the present invention will be described below. C: Cr, Mo, W, V, Nb7. , Contains at least 0.7% or more of C-C, which is necessary for base reinforcement of drill steel and NbC formation. Excess C of 1.2% or more
Since this impairs workability and toughness, the upper limit is set at 1.2%. Si: It is effective as a deoxidizing agent in steel manufacturing, and at the same time improves strength and softening resistance, but addition of a large amount impairs hot and cold workability, so the range is limited to 0.3 to 1.5%. do. Like Mn:Si, Mn is added as a deoxidizer on 5J14, but since it has little effect on improving wear resistance and toughness, its range is set to 1.0% or less. C": Mainly forms L3Cs carbide, and during quenching, most of it dissolves in the base, strengthening the base and increasing high temperature strength. Cr also has the effect of increasing hardenability. At least 433% Above 6% is necessary, and above 6% has no merits in terms of characteristics or economy, so the range should be reduced to 3%.
~6%. Mo: Increases the resistance to tempering and softening, and also increases the secondary effect, thereby imparting wear resistance. 6 Mo: 5.0% or more to obtain the hardness required for drill steel. However, if 10% or more, rod-shaped coarse M and C carbides are formed and the hardenability is deteriorated, so the optimum component range is set to 5.
.. 0 to 10.0%. W: Like Mo, increases temper hardening ability and softening resistance, and imparts heat resistance. At the same time, it mainly forms &+6C type carbides and provides wear resistance. If it is less than 1%, the effect will be small, and if it is more than 9%, hot workability will be impaired and M
, which causes coarsening of C-type carbides and impairs hardenability and toughness, so the range is set to 1.0 to 9.0%. V: A strong jl carbide-forming element in high-speed steel. If there are many additives, a large amount remains as undissolved residual carbide during quenching, which contributes to wear resistance. Also, V is
6 The Vl of the steel of the present invention, which contributes to secondary tempering hardening, is kept within a range that leaves almost no undissolved residual carbide after quenching, that is, within a range necessary for secondary tempering. VO15%
Below, the amount of carbide precipitated by tempering is small, so it is not possible to obtain a hardness of IIR (: 65 or higher) required for steel for drilling. At 1.25% or more, the undissolved residual coarse carbides are formed, and the grinding This range is set to 0.5, as it becomes a factor that inhibits sex.
~1.25%. Nb: Most of Nb forms stable and hard NbC carbide and does not dissolve into the matrix during quenching heating, improving wear resistance, which is one of the objectives of the present invention. On the other hand, the fine distribution has the effect of inhibiting the coarsening of crystal grains, thereby improving toughness. Below 0.3%, the effect is only 7f.
If it is less than 1.0%, the hardenability and ultimate hardness will be lowered, and at the same time, NbC carbides will become coarser, so the range is set to 0.3 to 1.0%. It has been found that the best relationship between wear resistance and toughness is given when the Nb/V ratio is 0.8 to 1.5%. Below .8,
As shown in the examples in Table 2 and the effects in Table 3, the toughness and cutting durability are reduced, and if the Nb/V ratio exceeds 1.5 and is added to the machine, the heat treatment hardness is insufficient and the jizz resistance is reduced. The Nb/V ratio should be 0.8 to 1.0 because wear resistance and cutting durability decrease.
It was limited to a range of 5. Co: Fully solid solution in the base, has the effect of strengthening the base and increasing the softening resistance, and has resistance to the upper temperature limit of the tool.In order to make the above effect effective, the Co content must be at least 65.0%. need to be added. The more Co there is, the more remarkable the effect is, but 1
Addition of 2.0% or more reduces hot and cold elongation, impairs workability, and is expensive, impairing economic efficiency, so it is set at 12.0% or less. [Example] Table 1 shows a 50 kg steel ingot produced in a vacuum melting furnace and forged. The chemical composition of the present invention steel and Hisame steel, which were made into φ20 round steel after rolling, are shown. Table 2 shows the quenching and tempering depth, austenite grain size, and bending fracture due to three-point bending load when φ20 test steel was heat-treated at a quenching temperature of 1200°C and annealing temperature of 560'Cx lH three times. The mating material S (1g
415, a friction speed of 0.24 m/sec, a friction distance of F' of 400 m, and a final load of 12.6 g. As shown in Table 2, the steel of the present invention has a hardness of HRC 65 or higher, which is required for drill steel, and has superior toughness and wear resistance to the comparative steel. Table 3 shows a φ6 straight drill made from the sample steel.
The cutting conditions that show the cutting durability when drilling with a drilling machine are: rotation speed 745r, p, m,
Cutting speed 14m/win, feed 0.15m*/"f!
V, the hole depth was 20 m5 + a through hole, and water-soluble cutting oil was used. The work material is 5tlS304. HB185
It's for you. Table 3 [Effect 1] According to the steel of the present invention, it is possible to obtain improvements in wear resistance and toughness that are necessary for steel for drills, so it can significantly improve the cutting life of difficult-to-process materials such as stainless steel. be able to.
Claims (1)
.30〜1.50%、Mn:1.0%以下、Cr:3.
0〜6.0%、Mo:5.0〜10.0%、W:1.0
〜9.0%、V:0.5〜1.25%、Nb:0.5〜
1.0%、Co:5.0〜12.0%、残部が鉄および
製鋼上不可避の不純物を含有する鋼であってNb/V比
が0.8〜1.5を満たすドリル用鋼。(1) In weight%, C: 0.70-1.20%, Si: 0
.. 30-1.50%, Mn: 1.0% or less, Cr: 3.
0-6.0%, Mo: 5.0-10.0%, W: 1.0
~9.0%, V: 0.5~1.25%, Nb: 0.5~
1.0%, Co: 5.0 to 12.0%, and the remainder contains iron and impurities inevitable in steelmaking, and the steel for drilling has a Nb/V ratio of 0.8 to 1.5.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1317685A JPH03180447A (en) | 1989-12-08 | 1989-12-08 | Drill steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1317685A JPH03180447A (en) | 1989-12-08 | 1989-12-08 | Drill steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH03180447A true JPH03180447A (en) | 1991-08-06 |
Family
ID=18090881
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1317685A Pending JPH03180447A (en) | 1989-12-08 | 1989-12-08 | Drill steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH03180447A (en) |
-
1989
- 1989-12-08 JP JP1317685A patent/JPH03180447A/en active Pending
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