US3165402A - Alloy steel and method of heat treatment therefor - Google Patents
Alloy steel and method of heat treatment therefor Download PDFInfo
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- US3165402A US3165402A US119276A US11927661A US3165402A US 3165402 A US3165402 A US 3165402A US 119276 A US119276 A US 119276A US 11927661 A US11927661 A US 11927661A US 3165402 A US3165402 A US 3165402A
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- the first method is to machine the die steel in its annealed or softened condition, and then heat-treat the machined die.
- the second method is to reverse the foregoing steps, that is, first heat-treat the die steel, and then machine it.
- the second method is not desirable because the heat treatment will raise the hardness to a level which makes the steel extremely difiicult to machine.
- a typical application in which a high hardness is necessary is a forging die which is subjected to high-impact loads.
- Typical applications for my new steel are dies and inserts for hot forging work, dies for extrusion work, and plastic molds and die casting dies.
- composition of my new alloy steel is substantially as follows, it being understood that the specified ranges are to be interpreted in the light of conventional check analyses tolerances.
- Carbon is essential in order to provide the necessary strength and hardness for the hot working applications mentioned above. If the carbon content is the field can be easily made.
- the steel becomes difficult to weld, and it is highly desirable that the steel be weldable so that cracks and repairs due to accidents or mishandling in If the carbon content is much below .35, it is diflicult to get the required hardness. 1 therefore limit the carbon content of my steel to the range of from about .35 to about .50, and preferably to a range of from about .37 to about .45.
- Manganese is necessary in order to reduce red shortness caused by sulphur. As is well known in the art,
- manganese readily combines with sulphur, and as a general rule, I find it desirable to add manganese in the ratio of 20 times the sulphur. I therefore desire from about .35 to about .60 percentmanganese. Any substantial quantity of manganese above .60 promotes an above normal number of non-metallic inclusions (i.e., the steel becomes dirty). If much below .35 manganese is added, the desired control of hot shortness not obtained with normal sulphur contents. I therefore limit my manganese to from about .35 to about .60 percent, and preferably from about .40 to about .60 percent.
- Phosphorous and sulphur are tramp elements in my steel, and should be kept at as low a level as economically feasible. Preferably, neither of these elements should exceed .025 percent.
- Silicon is necessary in order to increase the resistance to tempering of my steel. If much over 1 percent silicon is used, the steel tends to become brittle, whereas if much less than .40 percent is used, the silicon is ineffective to accomplish its desired result. silicon to the range of from about .40 to about 1.00 percent, and preferably to the range of from about .70 to about 1.00 percent.
- Nickel and chromium are both necessary in order to increase hardenability. With respect to this particular steel, I use the word hardenability to indicate hardness penetration in pieces of large cross section, not ability to harden. I have discovered that when the nickel and chromium content fall within rather well defined ranges, exceptional hardenability characteristics result. At the same time, however, the nickel content cannot be too high or the steel will become austenitic. Likewise, the chromium content cannot be too high or the steel will become non-hardenable. tent of my steel to the range of from about 3.00 to about 4.00 percent, and preferably from about 3.50 to about 4.00 percent, and chromium to the range of from about 1.00 to about 3.50 percent, and preferably to the range of from about 2.00 to about 2.50 percent. Hardness penetration through massive steel sections requires substantial amounts of nickel and chromium. Although they may be partially interchanged, amounts substantially below those indicated will not effect through hardening.
- Molybdenum and vanadium both increase resistance to softening and tempering. These elements also increase the secondary hardening effect which is one of the best characteristics of my steel. If either the molybdenum or vanadium contents are too high, however, the steel will become unhardenable. If the contents are too low, the necessary effects will not be obtained. I therefore limit my broad ranges of molybdenum and vanadium to the ranges of from about .50 to 1.00 and to from about .25 to about .40, respectively, and preferably to the ranges of from about .80 to about 1.00 and from about .25 to about .35, respectively.
- steel A is a steel falling within the scope of my invention and having the following composition:
- Steel B is a steel widely used in hot work applications, such ashammer forging dies, whose nominal ranges are as follows:
- I preferably austenitize my steel in the range of fromabout 1600 F. to about 1650 F., air harden the steel to at least a temperature at which it can be held in the hand (or, in other words, approximately room temperature) and then double temper the steel.
- the first temper should be at a temperature sufficient to condition the retained austenite. This temperature may vary somewhat from analysis to analysis-within my broad range,-
- the second tempering temperature should be sufficient to achieve the desired hardness. Again, this temperature may vary somewhat from analysis to analysis within my broad range, but a temperature in the rangeof from about 1000 F. to. l'100 P. will usually be quite satisfactory.
- a method of developing substantially uniform hardness in a piece of steel of large'cross section by heat treatment the composition of said steel: being substantially as follows in percent by weight:
- exceptional hardenability and good resistance to softening said method including the steps of sustenitizing the steel in the range of from about 1600" F., to about. 1650 F., air hardeningthe steel to approximately room temperature, and then double tempering the steel, the first tempering temperature being sumcient to condition the retained sustenite, and the. second tempering temperature being sufiicient'to achieve a desired, substantially uniform hardness throughout pieces of large cross section.
- An alloy steel consisting essentially. of, in percent by weight,about .35 to about .60 carbon, .35 to about .50 manganese, .40 to about 1.00 silicon, 3.00 to about 4.00 nickel, 1.00 to about 3.50 chromium, .50 to about 1.00 molybdenum, and .25 to about .40 vanadium, balance essentially iron, said steel being characterized by having good resistance .to abrasion and softening after prolonged exposure at elevated temperatures, and by excellent through hardness in large, mechanically worked cross sections when austenitiz ed in the range of from about 1600 F. to about 1650 F., air hardened to approximately room temperature and then double tempered.
- An alloy steel consisting essentially of, in percent by weight, about .37 to about .45 carbon, .40 to about .60 manganese, .70 to about 1.00 silicon, 3.50 to about 4.00 nickel, 2.00 to about 2.50 chromium, .80 to about 1.00 molybdenum, .25 to about35 vanadium, balance'essentially iron, said'steel being characterized by having good resistance toabrasion and softening after prolonged exposure at elevated temperature, and by excellent through hardness inlarge mechanically 'worked cross sections when austenitized in the range of from about 1600" F. to about 1650" F air hardened to approximately room temperature and then double tempered,
- a forgeable alloy steelhardenable by austenitizing in the range of from about 1600? F.-- to about 1650 F., air hardening to room temperature, and double tempering, and capable of retaining a through hardness of 3.50 to 3.75 Brinell' diameter after prolonged exposure at elevated temperature comprising, in percent by. weight, car- 5 bon .35 to about .60, manganese .35 to about .50, silico .40 to about 1.00, nickel 3.00 to about 4.00, chromium 1.00 to about 3.50, molybdenum .50 to about 1.00, and vanadium .25 to about .40, balance essentially iron.
- a mechanically Worked, hot Work implement of large cross section especially adapted for subjection to high impact loads of a repetitive nature under elevated temperature conditions and being characterized by having a substantially uniform through hardness of 3.50 to 3.75 Brinell diameter upon austenitizing, air hardening, and double tempering at a final temperature in the range of about 1000" F. to 1100 F., and comprising, in percent about .50, silicon .40 to about 1.00, nickel 3.00 to about 6 4.00, chromium 1.00 to about 3.50, molybdenum .50 to about 1.00, and vanadium .25 to about .40, balance essentially iron.
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- Heat Treatment Of Steel (AREA)
Description
United States Patent 3,165,402 ALLOY STEEL AND METHOD OF HEAT TREATMENT THEREFGR William F. Finkl, Chicago, Ill., assignor to A. Finkl & Sons, (10., a corporation of Illinois No Drawing. Filed June 26, 1961, Ser. No. 119,276 5 Claims. (Cl. 75-128) My invention relates to a new and improved low alloy steel, and particularly to a hot work steel having exceptional hardenability properties which makes it especially useful for hot work implements of large size.
There are two basic methods of preparing hot work implements used in metal shaping operations, such as forging. The first method is to machine the die steel in its annealed or softened condition, and then heat-treat the machined die. The second method is to reverse the foregoing steps, that is, first heat-treat the die steel, and then machine it.
In applications in which a very high hardness in the hot work implement is desired, the second method is not desirable because the heat treatment will raise the hardness to a level which makes the steel extremely difiicult to machine. A typical application in which a high hardness is necessary is a forging die which is subjected to high-impact loads.
To prepare a forging die from a die block, it is therefore necessary to first machine the steel in its annealed condition and then heat-treat it due to the machining difiiculties involved if the steel is first heat treated. In order to achieve the necessary hardness in the heat treatment, the steel is invariably quenched in oil or water. Such a quench is often undesirablebeoause the steel is thereby subjected to distortion and warping, and there is danger of cracking. If the die should crack, all of the time and effort expended in machining the die block is completely lost, and the die is a total loss except for its scrap value.
By contrast, my die steel, after being machined and then heat treated, will come out of a heat treating furnace at almost maximum hardness after a slow furnace cool. Usingsuch aslow cool minimizes distortion, warping and danger of cracking, and practically eliminates scrapping of the die due to the above-mentioned defects.
Typical applications for my new steel are dies and inserts for hot forging work, dies for extrusion work, and plastic molds and die casting dies.
The composition of my new alloy steel is substantially as follows, it being understood that the specified ranges are to be interpreted in the light of conventional check analyses tolerances.
Percent by weight Carbon .35-.50
Manganese .35-.60 Silicon .40-1.00 Nickel 3.'004.00 Chromium 1.00-3.50
Molybdenum .501.00 Vanadium .25-.40
Balance substantially all iron with the usual impurities.
Carbon, of course, is essential in order to provide the necessary strength and hardness for the hot working applications mentioned above. If the carbon content is the field can be easily made.
ice
much above .50, the steel becomes difficult to weld, and it is highly desirable that the steel be weldable so that cracks and repairs due to accidents or mishandling in If the carbon content is much below .35, it is diflicult to get the required hardness. 1 therefore limit the carbon content of my steel to the range of from about .35 to about .50, and preferably to a range of from about .37 to about .45.
Manganese is necessary in order to reduce red shortness caused by sulphur. As is well known in the art,
manganese readily combines with sulphur, and as a general rule, I find it desirable to add manganese in the ratio of 20 times the sulphur. I therefore desire from about .35 to about .60 percentmanganese. Any substantial quantity of manganese above .60 promotes an above normal number of non-metallic inclusions (i.e., the steel becomes dirty). If much below .35 manganese is added, the desired control of hot shortness not obtained with normal sulphur contents. I therefore limit my manganese to from about .35 to about .60 percent, and preferably from about .40 to about .60 percent.
Phosphorous and sulphur are tramp elements in my steel, and should be kept at as low a level as economically feasible. Preferably, neither of these elements should exceed .025 percent.
Silicon is necessary in order to increase the resistance to tempering of my steel. If much over 1 percent silicon is used, the steel tends to become brittle, whereas if much less than .40 percent is used, the silicon is ineffective to accomplish its desired result. silicon to the range of from about .40 to about 1.00 percent, and preferably to the range of from about .70 to about 1.00 percent.
Nickel and chromium are both necessary in order to increase hardenability. With respect to this particular steel, I use the word hardenability to indicate hardness penetration in pieces of large cross section, not ability to harden. I have discovered that when the nickel and chromium content fall within rather well defined ranges, exceptional hardenability characteristics result. At the same time, however, the nickel content cannot be too high or the steel will become austenitic. Likewise, the chromium content cannot be too high or the steel will become non-hardenable. tent of my steel to the range of from about 3.00 to about 4.00 percent, and preferably from about 3.50 to about 4.00 percent, and chromium to the range of from about 1.00 to about 3.50 percent, and preferably to the range of from about 2.00 to about 2.50 percent. Hardness penetration through massive steel sections requires substantial amounts of nickel and chromium. Although they may be partially interchanged, amounts substantially below those indicated will not effect through hardening.
Molybdenum and vanadium both increase resistance to softening and tempering. These elements also increase the secondary hardening effect which is one of the best characteristics of my steel. If either the molybdenum or vanadium contents are too high, however, the steel will become unhardenable. If the contents are too low, the necessary effects will not be obtained. I therefore limit my broad ranges of molybdenum and vanadium to the ranges of from about .50 to 1.00 and to from about .25 to about .40, respectively, and preferably to the ranges of from about .80 to about 1.00 and from about .25 to about .35, respectively.
I therefore limit I therefore limit the nickel conent from a study of the following tables. In the tables, steel A is a steel falling within the scope of my invention and having the following composition:
Carbon .396 Manganese .61 Silicon .65 Nickel 3.97 Chromium 2.90
Molybdenum 1.04 Vanadium .33
And the balance iron withthe usual impurities.
Steel B is a steel widely used in hot work applications, such ashammer forging dies, whose nominal ranges are as follows:
' Carbon. .50-.60. Manganese 65.90 Silicon 20135 Nickel .80.1.00 Chromium .801.10 Molybdenum .25-.35
And the'balance ironv with the usual impurities.
The unusualhardenability of my steel is indicated in the following table. A review of the data shows that the optimum annealing temperature is around 1100 F. to 1125 F. Even atthese temperatures the transformation is incomplete after 100 hours.
A comparison of my new steel to the standard steel with respect to resistance to tempering is set out below:
TABLE II Steel B Steel A Tempen, F.
1 Brinell diameter.
A comparison, of the Brinell diameter values in the above table will disclose that up to and including a tempering temperature of 1100 degrees, my new steel has a mailgedly higher resistance to tempering than the conventional steel; This shows that my new steel is more suitable than the standard steel for such applications as forging hammers in which the steel is subjected to high-impact loadsand alternate heating and cooling.
In order to achieve the good hardenability characteristics, I preferably austenitize my steel in the range of fromabout 1600 F. to about 1650 F., air harden the steel to at least a temperature at which it can be held in the hand (or, in other words, approximately room temperature) and then double temper the steel. The first temper should be at a temperature sufficient to condition the retained austenite. This temperature may vary somewhat from analysis to analysis-within my broad range,-
but a temperature onthe order of about 1000 F. will usually be quite satisfactory. The second tempering temperature should be sufficient to achieve the desired hardness. Again, this temperature may vary somewhat from analysis to analysis within my broad range, but a temperature in the rangeof from about 1000 F. to. l'100 P. will usually be quite satisfactory.
It should also be noted that my new steel will have extremely high resistance to abrasion. There is a substantial quantity of vanadium and molybdenum present, both of which are good carbide formers, and therefore it will resist washing very well. This,-of course, is important in repetitive applications, such as forging work.
Although I have illustrated and described preferred and specific embodiments of my invention, -itwill be understood that it is not so limited, and that slight modifications may be made by one skilled in the art without departing from the spirit of the invention. Accordingly, the scope of my invention should only be limited by the scope of the hereinafter appendedclaims.
I claim: a
1. A method of developing substantially uniform hardness in a piece of steel of large'cross section by heat treatment, the composition of said steel: being substantially as follows in percent by weight:
Carbon From about .35 to about .50 Manganese From about 35 to about .60 Silicon From about .40 to about 1.00 Nickel From about 3.00 to about 4.00 Chromium From about 1.00 to about 3.50 Molybdenum 'From about .50 to about 1.00 Vanadium. From'about .25 to about .40
and the balance substantially all iron,.said steel having,
exceptional hardenability and good resistance to softening, said method including the steps of sustenitizing the steel in the range of from about 1600" F., to about. 1650 F., air hardeningthe steel to approximately room temperature, and then double tempering the steel, the first tempering temperature being sumcient to condition the retained sustenite, and the. second tempering temperature being sufiicient'to achieve a desired, substantially uniform hardness throughout pieces of large cross section.
2. An alloy steel consisting essentially. of, in percent by weight,about .35 to about .60 carbon, .35 to about .50 manganese, .40 to about 1.00 silicon, 3.00 to about 4.00 nickel, 1.00 to about 3.50 chromium, .50 to about 1.00 molybdenum, and .25 to about .40 vanadium, balance essentially iron, said steel being characterized by having good resistance .to abrasion and softening after prolonged exposure at elevated temperatures, and by excellent through hardness in large, mechanically worked cross sections when austenitiz ed in the range of from about 1600 F. to about 1650 F., air hardened to approximately room temperature and then double tempered.
3. An alloy steel consisting essentially of, in percent by weight, about .37 to about .45 carbon, .40 to about .60 manganese, .70 to about 1.00 silicon, 3.50 to about 4.00 nickel, 2.00 to about 2.50 chromium, .80 to about 1.00 molybdenum, .25 to about35 vanadium, balance'essentially iron, said'steel being characterized by having good resistance toabrasion and softening after prolonged exposure at elevated temperature, and by excellent through hardness inlarge mechanically 'worked cross sections when austenitized in the range of from about 1600" F. to about 1650" F air hardened to approximately room temperature and then double tempered,
4. A forgeable alloy steelhardenable by austenitizing in the range of from about 1600? F.-- to about 1650 F., air hardening to room temperature, and double tempering, and capable of retaining a through hardness of 3.50 to 3.75 Brinell' diameter after prolonged exposure at elevated temperature comprising, in percent by. weight, car- 5 bon .35 to about .60, manganese .35 to about .50, silico .40 to about 1.00, nickel 3.00 to about 4.00, chromium 1.00 to about 3.50, molybdenum .50 to about 1.00, and vanadium .25 to about .40, balance essentially iron.
5. A mechanically Worked, hot Work implement of large cross section especially adapted for subjection to high impact loads of a repetitive nature under elevated temperature conditions and being characterized by having a substantially uniform through hardness of 3.50 to 3.75 Brinell diameter upon austenitizing, air hardening, and double tempering at a final temperature in the range of about 1000" F. to 1100 F., and comprising, in percent about .50, silicon .40 to about 1.00, nickel 3.00 to about 6 4.00, chromium 1.00 to about 3.50, molybdenum .50 to about 1.00, and vanadium .25 to about .40, balance essentially iron.
References Cited in the file of this patent UNITED STATES PATENTS 1,069,387 C-hurchward Aug. 5, 1913 2,012,765 Marthourey Aug. 27, 1935 2,279,716 Nieman Apr. 14, 1942 2,291,943 Bergen et al. Aug. 4, 1942 2,666,697 Elder et al Jan. 19, 1954 2,921,849 Furgason Jan. 19, 1960 2,996,376 Nehrenberg Aug. 15, 1961
Claims (1)
1. A METHOD OF DEVELOPING SUBSTANTIALLY UNIFORM HARDNESS IN A PIECE OF STEEL OF LARGE CROSS SECTION BY HEAT TREATMENT, THE COMPOSITION OF SAID STEEL BEING SUBSTANTIALLY AS FOLLOWS IN PERCENT BY WEIGHT:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US119276A US3165402A (en) | 1961-06-26 | 1961-06-26 | Alloy steel and method of heat treatment therefor |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US119276A US3165402A (en) | 1961-06-26 | 1961-06-26 | Alloy steel and method of heat treatment therefor |
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| Publication Number | Publication Date |
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| US3165402A true US3165402A (en) | 1965-01-12 |
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3379582A (en) * | 1967-02-15 | 1968-04-23 | Harry J. Dickinson | Low-alloy high-strength steel |
| US3431102A (en) * | 1966-10-20 | 1969-03-04 | Gen Dynamics Corp | Fusion welding filler metal with chromium nickel and vanadium alloying elements |
| US3507633A (en) * | 1967-04-17 | 1970-04-21 | Fernand J Dewez Jr | Circular saw blade of chromium nickel steel with an oxide coat |
| US3619179A (en) * | 1969-04-22 | 1971-11-09 | Allegheny Ludlum Steel | Age-hardening martensitic steels |
| US4170497A (en) * | 1977-08-24 | 1979-10-09 | The Regents Of The University Of California | High strength, tough alloy steel |
| US4170499A (en) * | 1977-08-24 | 1979-10-09 | The Regents Of The University Of California | Method of making high strength, tough alloy steel |
| US4861549A (en) * | 1988-02-18 | 1989-08-29 | National Forge Company | Roller caster shell steel |
| US5595614A (en) * | 1995-01-24 | 1997-01-21 | Caterpillar Inc. | Deep hardening boron steel article having improved fracture toughness and wear characteristics |
| US20060174737A1 (en) * | 2003-07-03 | 2006-08-10 | Seiko Epson Corporation | Manufacturing method of die for manufacturing liquid ejecting head, and material block used in the same |
| WO2009116933A1 (en) * | 2008-03-18 | 2009-09-24 | Uddeholm Tooling Aktiebolag | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
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| US1069387A (en) * | 1911-03-18 | 1913-08-05 | Churchward Internat Steel Company | Steel process. |
| US2012765A (en) * | 1928-12-11 | 1935-08-27 | Gennevilliers Acieries | Alloy steel, chiefly for use in the manufacture of railroad parts, rails, and the like |
| US2279716A (en) * | 1938-09-08 | 1942-04-14 | Bethlehem Steel Corp | Rail treatment |
| US2291943A (en) * | 1941-04-23 | 1942-08-04 | Crucible Steel Company | Process for producing high speed cutting tools |
| US2666697A (en) * | 1951-01-18 | 1954-01-19 | Louise J Eder | Ferrous alloys |
| US2921849A (en) * | 1959-06-08 | 1960-01-19 | Ladish Co | High strength alloy steels |
| US2996376A (en) * | 1961-04-06 | 1961-08-15 | Crucible Steel Co America | Low alloy steel having high hardness at elevated temperatures |
-
1961
- 1961-06-26 US US119276A patent/US3165402A/en not_active Expired - Lifetime
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1069387A (en) * | 1911-03-18 | 1913-08-05 | Churchward Internat Steel Company | Steel process. |
| US2012765A (en) * | 1928-12-11 | 1935-08-27 | Gennevilliers Acieries | Alloy steel, chiefly for use in the manufacture of railroad parts, rails, and the like |
| US2279716A (en) * | 1938-09-08 | 1942-04-14 | Bethlehem Steel Corp | Rail treatment |
| US2291943A (en) * | 1941-04-23 | 1942-08-04 | Crucible Steel Company | Process for producing high speed cutting tools |
| US2666697A (en) * | 1951-01-18 | 1954-01-19 | Louise J Eder | Ferrous alloys |
| US2921849A (en) * | 1959-06-08 | 1960-01-19 | Ladish Co | High strength alloy steels |
| US2996376A (en) * | 1961-04-06 | 1961-08-15 | Crucible Steel Co America | Low alloy steel having high hardness at elevated temperatures |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3431102A (en) * | 1966-10-20 | 1969-03-04 | Gen Dynamics Corp | Fusion welding filler metal with chromium nickel and vanadium alloying elements |
| US3379582A (en) * | 1967-02-15 | 1968-04-23 | Harry J. Dickinson | Low-alloy high-strength steel |
| US3507633A (en) * | 1967-04-17 | 1970-04-21 | Fernand J Dewez Jr | Circular saw blade of chromium nickel steel with an oxide coat |
| US3619179A (en) * | 1969-04-22 | 1971-11-09 | Allegheny Ludlum Steel | Age-hardening martensitic steels |
| US4170497A (en) * | 1977-08-24 | 1979-10-09 | The Regents Of The University Of California | High strength, tough alloy steel |
| US4170499A (en) * | 1977-08-24 | 1979-10-09 | The Regents Of The University Of California | Method of making high strength, tough alloy steel |
| US4861549A (en) * | 1988-02-18 | 1989-08-29 | National Forge Company | Roller caster shell steel |
| US5595614A (en) * | 1995-01-24 | 1997-01-21 | Caterpillar Inc. | Deep hardening boron steel article having improved fracture toughness and wear characteristics |
| US20060174737A1 (en) * | 2003-07-03 | 2006-08-10 | Seiko Epson Corporation | Manufacturing method of die for manufacturing liquid ejecting head, and material block used in the same |
| US7814640B2 (en) * | 2003-07-03 | 2010-10-19 | Seiko Epson Corporation | Manufacturing method of die for manufacturing liquid ejecting head, and material block used in the same |
| WO2009116933A1 (en) * | 2008-03-18 | 2009-09-24 | Uddeholm Tooling Aktiebolag | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
| EP2252717A1 (en) * | 2008-03-18 | 2010-11-24 | Uddeholms AB | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
| US20110000587A1 (en) * | 2008-03-18 | 2011-01-06 | Uddeholms Ab | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
| JP2011517729A (en) * | 2008-03-18 | 2011-06-16 | ウッデホルムス アーベー | Steel, steel blank manufacturing method, and method of manufacturing this steel part |
| US8562761B2 (en) * | 2008-03-18 | 2013-10-22 | Uddeholms Ab | Steel |
| RU2496907C2 (en) * | 2008-03-18 | 2013-10-27 | Уддехолмс АБ | Steel, method for making steel workpiece, and method for making part from above said steel |
| CN101978088B (en) * | 2008-03-18 | 2014-09-24 | 尤迪霍尔姆斯有限责任公司 | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
| EP2252717A4 (en) * | 2008-03-18 | 2014-10-01 | Uddeholms Ab | Steel, process for the manufacture of a steel blank and process for the manufacture of a component of the steel |
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