US3850621A - High-speed tool steels - Google Patents
High-speed tool steels Download PDFInfo
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- US3850621A US3850621A US00428312A US42831273A US3850621A US 3850621 A US3850621 A US 3850621A US 00428312 A US00428312 A US 00428312A US 42831273 A US42831273 A US 42831273A US 3850621 A US3850621 A US 3850621A
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- 229910000831 Steel Inorganic materials 0.000 title description 39
- 239000010959 steel Substances 0.000 title description 39
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 23
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 18
- 239000010703 silicon Substances 0.000 claims abstract description 18
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- 239000011651 chromium Substances 0.000 claims abstract description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910001315 Tool steel Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 239000011733 molybdenum Substances 0.000 claims abstract description 4
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 4
- 239000010937 tungsten Substances 0.000 claims abstract description 4
- 239000010941 cobalt Substances 0.000 claims abstract description 3
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 150000001247 metal acetylides Chemical class 0.000 description 9
- 238000005275 alloying Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000000227 grinding Methods 0.000 description 3
- 239000003921 oil Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 229910000997 High-speed steel Inorganic materials 0.000 description 2
- 238000007792 addition Methods 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000011362 coarse particle Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000006735 deficit Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
Definitions
- HIGH-SPEED TOOL STEELS This invention relates to high-speed steels having a high wear resistance combined with good machinability and ductility, and particularly relates to such steels wherein the silicon content is a function of the C/W/Mo/V content.
- High-speed tool steels are characterized by high re- 5 I sistance to wear up to working temperatures of 600C.
- the present invention is directed to solving the prob- 3 lem ofproducing high-speed tool steels which combine high wear resistance with good grindability and ductility.
- the present invention is based on the surprising discovery that provided certain alloying relationships are observed, namely in correlating thesilicon content to Steel No.
- the invention provides a high-speed tool steel possessing high wear resistance combined with good ductility and machin'ability, consisting essentially of balance iron,
- silicon content is not less than 0.5 percent and is determined by the formula Si 2.7 (%C) 0.1 (%W) 0.14 (%Mo) 0.5 @0113? 9-
- Si 2.7 (%C) 0.1 (%W) 0.14 (%Mo) 0.5 @0113? 9- By the term consisting essentially of in the Specification and claims hereof, is meant that impurities andabove the quantity as hereinbefore set forth leads to an undesirable carbide development and hence to an impairment of the properties of the steel. in such a case coarse primary carbides of the type M C and MC appear.
- the content limits of the silicon that is to be introduced according to the present'specification are calcu-.
- the contents of the alloying elements carbon.
- tungsten, molybdenum and vanadium the carbide proportion in the structure can be increased without the formation of carbides which by reason of their configuration and hardness impair grindability and ductility.
- This correlation between the said alloying components according to the invention permits a peritectoid carbide reaction to take place which leads to fine and evenly distributed carbides and hence improves grindability and ductility.
- FIG. 1 shows that the steel containing 0.26 percent Si solidifies with the formation of the spiculate M C carbide and that this remains stable up to high degrees of deformation (FIGS. la c).
- FIG. 2 shows that the Steel 1 having a silicon content according to the'above formula also solidifies via the M C eutectic but that its carbide is so unstable that this already decomposes as the ingot cools (FIG. 2a).
- This peritectoid decomposition becomes complete in the course of the following hot working process.
- Very fine and evenly distributed carbides of type M c and MC are formed, which impart to the Steel 1 a high resistance to wear coupled with good grindability and toughness.
- FIG. 3 demonstrates that silicon contents exceeding that calculated by the equation according to the invention lead to solidification of Steel 1 via the M C eutectic, giving rise to the appearance of coarse primary MC carbides (FIG. 30). These coarse carbides cannot be fully broken down even by considerable deformation, and they lead to the development of an irregular coarse-grained structure which adversely affects the properties of the said Steel 1.
- Silicon additions reduce the residual austenite which is present after the steels have been hardened. In order to mitigate this effect it is therefore advantageous to introduce into silicon-containing steels according to the invention nitrogen up to 0.] percent.
- the present invention enables high-speed tool steels of optimum structure and hence of outstanding applicational properties, such as toughness, wear resistance and grindability to be produced.
- improved wear resistance steels composed as proposed by the present invention surprisingly still prove to be readily grindable.
- steels of the proposed composition could be ground substantially without any difficulty.
- High-speed tool steels according to the invention are particularly suitable for the making of tools which call for a considerable amount of grinding to give them their final shape, particularly twist drills, taps, cutters, reamers and milling tools.
- silicon content is not less than 0.5 percent and is determined by the formula Si 2.7 (%C) 0.1 (%W) 0.14 (%Mo) 0.5 (%V) 0.3.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
Abstract
A high-speed tool steel possessing high wear resistance combined with good ductility and machinability, consisting essentially of 0.8 to 1.8 percent carbon, 3.5 to 10 percent chromium, 1 to 13 percent tungsten, 1-10 percent molybdenum, 0.5 to 5 percent vanadium, 0 to 10 percent cobalt, balance iron, wherein the silicon content is not less than 0.5 percent and is determined by the formula: % Si 2.7 (%C) - 0.1 (%W) - 0.14 (%Mo) - 0.5 (%V) + 0.3.
Description
United States Patent 191 Haberling et al.
1 HIGH-SPEED TOOL STEELS [75] Inventors: Edmund Haberling; Heinrich Kiesheyer, both of Krefeld; Hanshermann Weigand, Tonisvorst, all of Germany [73] Assignee: Deutsche Edelstahlwerke Gesellschaft mit beschrankter Haftung, Krefeld, Germany 22 Filed: Dec. 26, 1973 211 Appl. No.: 428,312
[30] Foreign Application Priority Data Dec. 27, 1972 Germany 2263576 [52] US. Cl. 75/126 A, 75/126 C, 75/126 E, 7 75/126 H, 75/126 .1, 75/126 Q [51] Int. Cl. C22c 39/14 [58] Field of Search 75/126 A, 126 C, 126 E, 75/126 H, 126 1,126 O [56] References Cited UNlTED STATES PATENTS 2,241,187 5/1941 De Vries 75/126 0 [451 Nov. 26, 1974 1/1967 Steven 75/126 Q 5/1974 Steven 75/126 A Primary ExaminerL. Dewayne Rutledge Assistant ExaminerArthur J. Steiner Attorney, Agent, or Firm-Cushman, Darby & Cushman [57] ABSTRACT 3 Claims, 3 Drawing Figures grind and also reduces their toughness.
HIGH-SPEED TOOL STEELS This invention relates to high-speed steels having a high wear resistance combined with good machinability and ductility, and particularly relates to such steels wherein the silicon content is a function of the C/W/Mo/V content.
High-speed tool steels are characterized by high re- 5 I sistance to wear up to working temperatures of 600C.
higher vanadium contents up to 5 percent, and higher corresponding percentages of carbon. Although such steels are highly wear-resisting, their high content of coarse particles of vanadium carbide, which has a hardness of about 3000 Vickers, makes them difficult to Recently the carbide content, and hence the wear resistance, has been raised by increasing the carbon content. Examples embodying such practice are the steels which in the A151 designation are known as M 41 and M 45, and which have vanadium contents of l to 2 percent with carbon contents between 1.1 and 1.2 percent. However it has been found that an increase in carbon leads to the development of spiculate carbides of the type M C, instead of the usual high-speed steel carbide M C (DEW Technical Reports 12, 1972, pp 111/33), and their hardness of around 2000 Vickers and unfavourable shape also adversely affect grindability and ductility.
The present invention is directed to solving the prob- 3 lem ofproducing high-speed tool steels which combine high wear resistance with good grindability and ductility.
The present invention is based on the surprising discovery that provided certain alloying relationships are observed, namely in correlating thesilicon content to Steel No.
. 2. pletely decomposes in a peritectoid reaction to the MC- and M C carbides which then appear in the desired form and distribution.
The invention provides a high-speed tool steel possessing high wear resistance combined with good ductility and machin'ability, consisting essentially of balance iron,
wherein the silicon content is not less than 0.5 percent and is determined by the formula Si 2.7 (%C) 0.1 (%W) 0.14 (%Mo) 0.5 @0113? 9- By the term consisting essentially of in the Specification and claims hereof, is meant that impurities andabove the quantity as hereinbefore set forth leads to an undesirable carbide development and hence to an impairment of the properties of the steel. in such a case coarse primary carbides of the type M C and MC appear.
l sman insla zlsa; H V
The content limits of the silicon that is to be introduced according to the present'specification are calcu-.
' lated from the equation hereinbefore set forth by reference to the limits in the content ranges of the melting y si g aa tsa nattisul rly we!!! The compositions of the examined steels within the ranges embraced by the invention are listed in the ac- C Cr W Mo V C0 Si 1 1.05 4.5 1.3 9.1 1.05 7. balance 1.03 1.10 5.5 1.5 2.5. 1.25 8.4 1.35 2 0.98 4.0 6.2 .0 1.75 .l. balance 0.56 1.03 4.5 6.5 5.25 2.0 0.59 3 0.98 4.0 1.5 8.0 1.75 V .l. balance 0.59 1.03 4.5 1.75 .5 2.0 0.94 4 0.97 5.0 2.5 2.75 2.25 J. balance 0.97 1.03 5.5 2.8 3.0 2.5 1.32
based on thg stated w limits of C. W. Mu. V l g to the w as herein set forth. W W
the contents of the alloying elements carbon. tungsten, molybdenum and vanadium, the carbide proportion in the structure can be increased without the formation of carbides which by reason of their configuration and hardness impair grindability and ductility. This correlation between the said alloying components according to the invention permits a peritectoid carbide reaction to take place which leads to fine and evenly distributed carbides and hence improves grindability and ductility.
The addition of exactly predetermined quantities of silicon according to the invention enables the carbon content to be raised and so adjusted thatalthough the carbide M C does form during solidification, it is so unstable that upon reheating prior to hot forming it comaccompanying drawings at a magnification x 500, of
which FIG. 1 shows that the steel containing 0.26 percent Si solidifies with the formation of the spiculate M C carbide and that this remains stable up to high degrees of deformation (FIGS. la c).
FIG. 2 shows that the Steel 1 having a silicon content according to the'above formula also solidifies via the M C eutectic but that its carbide is so unstable that this already decomposes as the ingot cools (FIG. 2a). This peritectoid decomposition becomes complete in the course of the following hot working process. Very fine and evenly distributed carbides of type M c and MC (FIGS. 2b and c) are formed, which impart to the Steel 1 a high resistance to wear coupled with good grindability and toughness.
FIG. 3 demonstrates that silicon contents exceeding that calculated by the equation according to the invention lead to solidification of Steel 1 via the M C eutectic, giving rise to the appearance of coarse primary MC carbides (FIG. 30). These coarse carbides cannot be fully broken down even by considerable deformation, and they lead to the development of an irregular coarse-grained structure which adversely affects the properties of the said Steel 1.
The majority of conventional high-speed tool steels have silicon contents that are too low for an optimal development of the carbides. If the present invention is applied to such steels their properties are improved, as illustrated by the following results.
With Steel 2, the plastic bending effort in a static bending test was determined. The Steel 2 had been heat-treated as follows: Hardened by oil quenching from 1,200C; tempered at 560C for two periods of one hour. The measured value was 2.5 .I. By comparison the corresponding values of steels similar to Steel 2 but containing only 0.3 percent Si and 1.8 percent Si, were about 2 J.
In order to test ductility and cutting performance planing tests were carried outwith Steel 3. A tool made of the said Steel 3 was hardened by oil quenching from l,200C. and tempered at 550C. for two periods of one hour. The wear on the underface was measured after 1000 strokes (equivalent to 450 metres total length of cut). The wear in Steel 3 was found to be 0.1 mm. Compared with this result steels similar to Steel 3 but containing 0.3 percent and 1.8 percent Si, showed twice as much wear, viz. 0.2 mm.
In a turning test on blanks made of Steel 4, the durability, i.e., the cutting speed in m/min at which the tool failed, i.e.. became useless in 30 minutes machining, was highest with a time of 19.5 m/min when the silicon content had been adjusted to the contents of the other alloying elements according to the invention. The tools made of Steel 4 were hardened by oil quenching from l,200C. and tempered at 540C. for two periods of one hour. However tests on steels of the composition similar toSteel 4, but in one instance containing 1.8 percent Si, and in another instance 0.3 percent Si, gave V60 durability test results of l9 m/min and I8 m/min.
properties is obtained. Increased silicon contents lead to greater hardness but they cause a shift of the secondary hardness maximum to lower annealing temperatures. This reduction in temper stability due to the silicon is a disadvantage in the use of such steels. It has been found that this disadvantage may be overcome by means of further alloying procedures and that the reduction in temper stability due to the silicon can be improved by raising the chromium content of the steels which is normally about 4 percent to higher values.
Thus in a preferred embodiment of the invention the optimum chromium content to ensure stability to temper should be related to the silicon content of the steel by the formula Cr=4 2 (%Si).
Silicon additions reduce the residual austenite which is present after the steels have been hardened. In order to mitigate this effect it is therefore advantageous to introduce into silicon-containing steels according to the invention nitrogen up to 0.] percent.
The present invention enables high-speed tool steels of optimum structure and hence of outstanding applicational properties, such as toughness, wear resistance and grindability to be produced. Despite their improved wear resistance steels composed as proposed by the present invention surprisingly still prove to be readily grindable. Whereas with grinding steels of corresponding other compositions the grinding wheels quickly choked and became blunted causing inadmissible heating and scorching of the ground tools, steels of the proposed composition could be ground substantially without any difficulty.
High-speed tool steels according to the invention are particularly suitable for the making of tools which call for a considerable amount of grinding to give them their final shape, particularly twist drills, taps, cutters, reamers and milling tools.
What is claimed is:
I. A high-speed tool steel possessing high wear resistance combined with good ductility and machinability, consisting essentially of 0.8 to 1.8 '/1 carbon,
3.5 to l0 /1 chromium.
l to l3 tungsten,
l to 10 /1 molybdenum. 0.5 [0 5 71 vanadium. 0 to 10 "/1 cobalt.
balance iron.
wherein the silicon content is not less than 0.5 percent and is determined by the formula Si 2.7 (%C) 0.1 (%W) 0.14 (%Mo) 0.5 (%V) 0.3.
2. A high-speed tool steel according to claim 1, wherein the chromium content is adjusted by reference to the silicon content according to the formula Cr=4+2 (%Si).
3. A high-speed tool steel according to claim 1,
wherein it contains up to 0.l percent nitrogen.
- l l =l
Claims (3)
1. A HIGH-SPEED TOOL STEEL POSSESSING HIGH WEAR RESISTANCE COMBINED WITH GOOD DUCTILITY AND MACHINABILITY CONSISTING ESSENTIALLY OF 0.8 TO 1.8 % CARBON. 3.5 TO 10 % CHROMIUM, 1 TO 13 % TUNGSTEN, 1 TO 10 % MOLYBDENUM, 0.5 TO 5 %VANADIUM, 0 TO 10 % COBALT, BALANCE IRON, WHEREIN THE SILCON CONTENT IS NOT LESS THAN 0.5 PERCENT AND IS DETERMINED BY THE FORMULA
2. A high-speed tool steel according to claim 1, wherein the chromium content is adjusted by reference to the silicon content according to the formula % Cr 4 + 2 (%Si).
3. A high-speed tool steel according to claim 1, wherein it contains up to 0.1 percent nitrogen.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE2263576A DE2263576B2 (en) | 1972-12-27 | 1972-12-27 | Process for producing an M2 C-free structure in high-speed steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3850621A true US3850621A (en) | 1974-11-26 |
Family
ID=5865536
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US00428312A Expired - Lifetime US3850621A (en) | 1972-12-27 | 1973-12-26 | High-speed tool steels |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US3850621A (en) |
| JP (1) | JPS4997719A (en) |
| AT (1) | AT348566B (en) |
| DE (1) | DE2263576B2 (en) |
| FR (1) | FR2212440B1 (en) |
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
| US4116684A (en) * | 1976-03-17 | 1978-09-26 | Hitachi Metals, Ltd. | High speed tool steel having high toughness |
| US4242130A (en) * | 1977-12-27 | 1980-12-30 | Thyssen Edelstahlwerke Ag | High-speed steel |
| US4276085A (en) * | 1976-11-22 | 1981-06-30 | Uddeholms Aktiebolag | High speed steel |
| US4780139A (en) * | 1985-01-16 | 1988-10-25 | Kloster Speedsteel Ab | Tool steel |
| US5063116A (en) * | 1990-03-16 | 1991-11-05 | Hitachi Metals, Ltd. | Wire for dot printer |
| US5674449A (en) * | 1995-05-25 | 1997-10-07 | Winsert, Inc. | Iron base alloys for internal combustion engine valve seat inserts, and the like |
| US6057045A (en) * | 1997-10-14 | 2000-05-02 | Crucible Materials Corporation | High-speed steel article |
| US6200528B1 (en) | 1997-09-17 | 2001-03-13 | Latrobe Steel Company | Cobalt free high speed steels |
| US6200394B1 (en) * | 1997-05-08 | 2001-03-13 | Research Institute Of Industrial Science & Technology | High speed tool steel |
| US6723182B1 (en) | 2002-11-14 | 2004-04-20 | Arthur J. Bahmiller | Martensitic alloy steels having intermetallic compounds and precipitates as a substitute for cobalt |
| US20060283526A1 (en) * | 2004-07-08 | 2006-12-21 | Xuecheng Liang | Wear resistant alloy for valve seat insert used in internal combustion engines |
| US20070160490A1 (en) * | 2006-01-09 | 2007-07-12 | Ati Properties, Inc. | Tool and bearing steels |
| US20100011594A1 (en) * | 2008-07-15 | 2010-01-21 | Wysk Mark J | Composite Saw Blades |
| US9334547B2 (en) | 2013-09-19 | 2016-05-10 | L.E. Jones Company | Iron-based alloys and methods of making and use thereof |
| CN108315664A (en) * | 2018-04-26 | 2018-07-24 | 河冶科技股份有限公司 | Thread rolling plate material and preparation method thereof |
| US12234536B2 (en) | 2022-12-03 | 2025-02-25 | Arthur Craig Reardon | High speed steel composition |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52141406A (en) * | 1976-05-21 | 1977-11-25 | Kobe Steel Ltd | Tool steel containing nitrogen made by powder metallurgy |
| SE400093B (en) * | 1976-07-09 | 1978-03-13 | Fagersta Ab | LEGAL ALLOY SPEED |
| FR2601268B1 (en) * | 1986-07-11 | 1992-07-24 | Chavanne Ketin | COMPOSITE STEEL WORKING CYLINDER FOR HOT TRAIN. |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2241187A (en) * | 1937-12-27 | 1941-05-06 | Allegheny Ludlum Steel | Alloy steel |
| US3295966A (en) * | 1964-04-30 | 1967-01-03 | Crucible Steel Co America | Versatile low-alloy tool steel |
| US3809541A (en) * | 1972-10-24 | 1974-05-07 | G Steven | Vanadium-containing tool steel article |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR800098A (en) * | 1935-12-28 | 1936-06-26 | Cleveland Twist Drill Co | Alloys and products obtained therefrom |
| US2212227A (en) * | 1939-07-08 | 1940-08-20 | Allegheny Ludlum Steel | High speed tool |
| US2212228A (en) * | 1940-06-12 | 1940-08-20 | Allegheny Ludlum Steel | Alloy steel |
| SU210378A1 (en) * | 1966-03-09 | 1968-02-06 | Л. А. Позн Ю. М. Скрынченко, В. Ф. Смол ков, Г. Габуев, В. П. Францов , А. И. Хнтрик | STAMP STEEL |
| SU203918A1 (en) * | 1966-12-28 | 1967-10-09 | Б. Л. Александрович, Ю. А. Геллер , Л. С. Кремнев Московский станкоинструментальный институт | QUICKLINE STEEL |
-
1972
- 1972-12-27 DE DE2263576A patent/DE2263576B2/en not_active Ceased
-
1973
- 1973-12-19 FR FR7345449A patent/FR2212440B1/fr not_active Expired
- 1973-12-21 AT AT1077273A patent/AT348566B/en not_active IP Right Cessation
- 1973-12-26 US US00428312A patent/US3850621A/en not_active Expired - Lifetime
- 1973-12-27 JP JP49004528A patent/JPS4997719A/ja active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2241187A (en) * | 1937-12-27 | 1941-05-06 | Allegheny Ludlum Steel | Alloy steel |
| US3295966A (en) * | 1964-04-30 | 1967-01-03 | Crucible Steel Co America | Versatile low-alloy tool steel |
| US3809541A (en) * | 1972-10-24 | 1974-05-07 | G Steven | Vanadium-containing tool steel article |
Cited By (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
| US4116684A (en) * | 1976-03-17 | 1978-09-26 | Hitachi Metals, Ltd. | High speed tool steel having high toughness |
| US4276085A (en) * | 1976-11-22 | 1981-06-30 | Uddeholms Aktiebolag | High speed steel |
| US4242130A (en) * | 1977-12-27 | 1980-12-30 | Thyssen Edelstahlwerke Ag | High-speed steel |
| US4780139A (en) * | 1985-01-16 | 1988-10-25 | Kloster Speedsteel Ab | Tool steel |
| US5063116A (en) * | 1990-03-16 | 1991-11-05 | Hitachi Metals, Ltd. | Wire for dot printer |
| US5674449A (en) * | 1995-05-25 | 1997-10-07 | Winsert, Inc. | Iron base alloys for internal combustion engine valve seat inserts, and the like |
| US6200394B1 (en) * | 1997-05-08 | 2001-03-13 | Research Institute Of Industrial Science & Technology | High speed tool steel |
| US6200528B1 (en) | 1997-09-17 | 2001-03-13 | Latrobe Steel Company | Cobalt free high speed steels |
| US6057045A (en) * | 1997-10-14 | 2000-05-02 | Crucible Materials Corporation | High-speed steel article |
| US6723182B1 (en) | 2002-11-14 | 2004-04-20 | Arthur J. Bahmiller | Martensitic alloy steels having intermetallic compounds and precipitates as a substitute for cobalt |
| US20060283526A1 (en) * | 2004-07-08 | 2006-12-21 | Xuecheng Liang | Wear resistant alloy for valve seat insert used in internal combustion engines |
| US7611590B2 (en) | 2004-07-08 | 2009-11-03 | Alloy Technology Solutions, Inc. | Wear resistant alloy for valve seat insert used in internal combustion engines |
| US20070160490A1 (en) * | 2006-01-09 | 2007-07-12 | Ati Properties, Inc. | Tool and bearing steels |
| US7387692B2 (en) | 2006-01-09 | 2008-06-17 | Ati Properties, Inc. | Tool and bearing steels |
| US20100011594A1 (en) * | 2008-07-15 | 2010-01-21 | Wysk Mark J | Composite Saw Blades |
| US20140102276A1 (en) * | 2008-07-15 | 2014-04-17 | Irwin Industrial Tool Company | Composite Saw Blades |
| US9334547B2 (en) | 2013-09-19 | 2016-05-10 | L.E. Jones Company | Iron-based alloys and methods of making and use thereof |
| US9932867B2 (en) | 2013-09-19 | 2018-04-03 | L.E. Jones Company | Iron-based alloys and methods of making and use thereof |
| CN108315664A (en) * | 2018-04-26 | 2018-07-24 | 河冶科技股份有限公司 | Thread rolling plate material and preparation method thereof |
| US12234536B2 (en) | 2022-12-03 | 2025-02-25 | Arthur Craig Reardon | High speed steel composition |
Also Published As
| Publication number | Publication date |
|---|---|
| ATA1077273A (en) | 1976-10-15 |
| JPS4997719A (en) | 1974-09-17 |
| FR2212440A1 (en) | 1974-07-26 |
| FR2212440B1 (en) | 1977-06-10 |
| AT348566B (en) | 1979-02-26 |
| DE2263576A1 (en) | 1974-07-11 |
| DE2263576B2 (en) | 1978-06-01 |
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