US2793113A - Creep resistant steel - Google Patents
Creep resistant steel Download PDFInfo
- Publication number
- US2793113A US2793113A US375562A US37556253A US2793113A US 2793113 A US2793113 A US 2793113A US 375562 A US375562 A US 375562A US 37556253 A US37556253 A US 37556253A US 2793113 A US2793113 A US 2793113A
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- US
- United States
- Prior art keywords
- alloy
- titanium
- ferritic
- creep
- resistance
- 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.)
- Expired - Lifetime
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- 229910000831 Steel Inorganic materials 0.000 title description 5
- 239000010959 steel Substances 0.000 title description 5
- 229910045601 alloy Inorganic materials 0.000 description 18
- 239000000956 alloy Substances 0.000 description 18
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 12
- 239000010936 titanium Substances 0.000 description 12
- 229910052719 titanium Inorganic materials 0.000 description 12
- 239000010955 niobium Substances 0.000 description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 8
- 229910052804 chromium Inorganic materials 0.000 description 8
- 239000011651 chromium Substances 0.000 description 8
- 229910052758 niobium Inorganic materials 0.000 description 8
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 6
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 6
- 229910000851 Alloy steel Inorganic materials 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 230000035882 stress Effects 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 229910052715 tantalum Inorganic materials 0.000 description 4
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 3
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 229910052735 hafnium Inorganic materials 0.000 description 3
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- 239000010937 tungsten Substances 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 230000001419 dependent effect Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- MGRWKWACZDFZJT-UHFFFAOYSA-N molybdenum tungsten Chemical compound [Mo].[W] MGRWKWACZDFZJT-UHFFFAOYSA-N 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical compound OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- YNZRYCGVGOAAKO-UHFFFAOYSA-N [N].[Mo].[W] Chemical compound [N].[Mo].[W] YNZRYCGVGOAAKO-UHFFFAOYSA-N 0.000 description 1
- AXSCZBBSHYVKKU-UHFFFAOYSA-N [Zr].[Si].[Ca] Chemical compound [Zr].[Si].[Ca] AXSCZBBSHYVKKU-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- RYTYSMSQNNBZDP-UHFFFAOYSA-N cobalt copper Chemical compound [Co].[Cu] RYTYSMSQNNBZDP-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical group [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
Definitions
- This invention relates to ferritic alloy steels having tried h, for p e12% hr l y nimproved resistance to scaling and creep deformation at high temperatures.
- a ferritic alloy we mean one which consists of an iron-rich matrix with excess carbide or other compounds taining niobium shown at C in the table. A substantially increased creep resistance has thus been obtained but one which still gives scope for much improvement.
- thedesirable treatment of such as dispersed particles Compounds, other than carbides, alloys Consists of a high temperature 801115011 treatment which may be present include nitrides, borides, and intermetallic compounds such, for example, as FeCr commonly referred to as sigma phase in ferrous alloys having high chromium contents.
- the matrix is usually in followed by a tempering or ageing treatment.
- the solution treatment may be carried out above 1150 C. provided the temperature employed avoids overheating, burning, or excessive grain coarsening. It is the body-centred cubic condition but may be more-or also well known that the addition Of 12% chromium 10 less distorted by heat treatment; for example, after a.
- martensite tetragonal form
- Such an alloy is magnetic at room temperature and will, on heating, transform into the noniron decreases the temperature and composition ranges at which austenite is stable. Since the creep resistance prop erties of these alloys depend on the different solubilities of carbon in ferrite and austenite, an alloy which does magnetic face-centred cubic condition known as austenite not become Wholly austenitic at the Solution frfiatmcnt and revert to the magnetic form on cooling.
- Some ferritic steels are hardenable by heat-treatment; others are not. When hardened, they may assume a variety of forms known as martensite, bainite, troostite, sorbite, pearlite,
- the carbide formers can, for ex ample, be titanium, vanadium, and niobium.
- the use of titanium enables a reduced amount of niobium and vanadium to be employed with a further substantial inthe optimum amount of carbide of a face-centred cubic crease increep resistance-see the alloy shown at E in structure is formed, i. e. so that the carbides present have a structure similar to that of sodium chloride.
- the creep resistance is dependent upon the combination of the constitution of the matrix, the crystal form, size disthe table. A still further increase in creep resistance is obtained by the addition of boron as shown at F in the table. i
- titanium as a carbide former is of the greattribution and composition of the carbides, these factors estimportance both technically and commercially. Techbeing dependent upon the manner in which the alloy is heat treated.
- Patented May 21, 1957 its importance is that it is both cheap and abundant in comparison with niobium and tantalum and, as its use allows the amounts of the latter elements to be substantially reduced, it has a substantial bearing on the cost of production of the alloys.
- titanium is preferably made as titanium metal to the molten steel after deoxidation of the bath by means of calcium-silicon-Zirconium or other suitable deoxidant.
- Ferro-titanium may be used but the titanium metal is preferred since ferro-titanium commonly contains impurities which may have a deleterious effect on the creep resistance.
- Three or more carbide formers including titanium and selected from vanadium, niobium, tantalum, titanium, hafnium, zirconium 0.05-4.0
- the alloys may also usefully contain:
- the heat treatment of such an alloy- should comprise a high temperature treatment followed by a tempering or ageing treatment.
- the alloys in accordance with the invention can be used under high stress and high temperature conditions such as occur in gas turbines and other applications.
- a disc approximately .24 inches in diameter and 2 inches thick with an integral boss 8 inches in diameter and 4 /2 inches thick was forged from an ingot inches square of a steel manufactured by the basic electric arc process having the following percentage composition:
- the disc was quenched from 1250" C. and tempered for 48 hours at 650 C. It was then found to have the following properties:
- a ferritic alloy steel according to claim 1 containing also any one or more of the following:
- tungsten not greater than 2%) and molybdenum tungsten (not greater than 4%), from 0.05 to 4% of at least three face centered cubic carbide formers including titanium and selected from the group consisting of titanium, vanadium, niobium, tantalum, hafnium, and zirconium, the balance substantially iron.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Description
CREEP RESISTANT STEEL John R. Rait and John 0. Ward, Sheflield, England, as-
signors to Hadfields Limited, Sheilield, England No Drawing. Application August 20, 1953,
Serial No. 375,562
Claims priority, application Great Britain August 22, 1952 .4 Claims. (Cl. 75-128) nited States Patent ent when a smaller proportion of chromium is used and,
in fact, leads to the formation of two chromium types of carbides, one having a trigonal structure and the other a complex cubic structure. The use of other elements forming face-centred cubic carbides has, therefore, been This invention relates to ferritic alloy steels having tried h, for p e12% hr l y nimproved resistance to scaling and creep deformation at high temperatures.
By a ferritic alloy we mean one which consists of an iron-rich matrix with excess carbide or other compounds taining niobium shown at C in the table. A substantially increased creep resistance has thus been obtained but one which still gives scope for much improvement.
It is well known that thedesirable treatment of such as dispersed particles. Compounds, other than carbides, alloys Consists of a high temperature 801115011 treatment which may be present include nitrides, borides, and intermetallic compounds such, for example, as FeCr commonly referred to as sigma phase in ferrous alloys having high chromium contents. The matrix is usually in followed by a tempering or ageing treatment. For example, the solution treatment may be carried out above 1150 C. provided the temperature employed avoids overheating, burning, or excessive grain coarsening. It is the body-centred cubic condition but may be more-or also well known that the addition Of 12% chromium 10 less distorted by heat treatment; for example, after a. very rapid cool, it may take the tetragonal form known as martensite. Such an alloy is magnetic at room temperature and will, on heating, transform into the noniron decreases the temperature and composition ranges at which austenite is stable. Since the creep resistance prop erties of these alloys depend on the different solubilities of carbon in ferrite and austenite, an alloy which does magnetic face-centred cubic condition known as austenite not become Wholly austenitic at the Solution frfiatmcnt and revert to the magnetic form on cooling. Some ferritic steels are hardenable by heat-treatment; others are not. When hardened, they may assume a variety of forms known as martensite, bainite, troostite, sorbite, pearlite,
temperature but develops a duplex ferritic-austenitic structure, cannot develop its optimum properties. The alloy shown at C in the table is prone to form this duplex structure on heating; to the 'desired temperatures for and so on. One ferritic alloy which has been propos d carbide solution. The ferritic tendency may be avoided for service at high temperatures up to about 700C. has a chromium content of 3% and consists principally of carbide formers and ferrite strengtheners, no attention being given to scale resistance. An example of it is shown at A in the following table:
Table by the addition of nitrogen or nickel or other austenitising elements and a very substantial increase in creep resistance be thereby obtained as can be seen from the alloy shown at D in the table.
40 Whereas the cubic carbide has formerly been provided The alloy shown at A and, generally speaking, .all
Total Creep Deformation, per- Comparative cent at times Creep Re- Analysls stated under a sistance tensile stress of based on8 8 tons/sq. in. at tons/sq. in. 600 C.
and 300 hrs.
0 Cr Mo W V Nb Ti N B 300 hrs 1000 hrs by two carbide formers, i. e. niobium and vanadium, we
similar ferritic alloys with good creep resistance have finclthat a mixture ofthree or more face-centred cubic poor scaling resistance.
It has been clearly shown in published work thatif such an alloy is to have a good creep resistance at high temperatures, its composition must be adjusted so that carbides is preferable. The carbide formers can, for ex ample, be titanium, vanadium, and niobium. The use of titanium enables a reduced amount of niobium and vanadium to be employed with a further substantial inthe optimum amount of carbide of a face-centred cubic crease increep resistance-see the alloy shown at E in structure is formed, i. e. so that the carbides present have a structure similar to that of sodium chloride. The creep resistance is dependent upon the combination of the constitution of the matrix, the crystal form, size disthe table. A still further increase in creep resistance is obtained by the addition of boron as shown at F in the table. i
The use of titanium as a carbide former is of the greattribution and composition of the carbides, these factors estimportance both technically and commercially. Techbeing dependent upon the manner in which the alloy is heat treated.
nically, as canbe seenffrom the table, it leads to a very substantial increase, in creep resistance. Commercially,
Patented May 21, 1957 its importance is that it is both cheap and abundant in comparison with niobium and tantalum and, as its use allows the amounts of the latter elements to be substantially reduced, it has a substantial bearing on the cost of production of the alloys.
The addition of the titanium is preferably made as titanium metal to the molten steel after deoxidation of the bath by means of calcium-silicon-Zirconium or other suitable deoxidant. Ferro-titanium may be used but the titanium metal is preferred since ferro-titanium commonly contains impurities which may have a deleterious effect on the creep resistance.
The table given above gives in Examples E and F the analysis of particular alloys in accordance with the invention and is concerned only with essential elements. In general, the invention extends to ferritic steel alloys having 'high creep resistance and scaling resistance at temperatures up to about 700 C. and having as essential constituents:
Percent Carbon 0.05-0.50 Chromium 8.0-17.0 Molybdenum 4.0
or Tungsten 2.0
Molybdenum Tungsten Nitrogen 0.01-0.25 Silicon 0.1- 2.0 Manganese 0.1- 4.0
Three or more carbide formers including titanium and selected from vanadium, niobium, tantalum, titanium, hafnium, zirconium 0.05-4.0
The alloys may also usefully contain:
And unavoidable impurities.
The heat treatment of such an alloy-should comprise a high temperature treatment followed by a tempering or ageing treatment.
The alloys in accordance with the invention can be used under high stress and high temperature conditions such as occur in gas turbines and other applications.
The following is a typical example of results obtained from the invention:
A disc approximately .24 inches in diameter and 2 inches thick with an integral boss 8 inches in diameter and 4 /2 inches thick Was forged from an ingot inches square of a steel manufactured by the basic electric arc process having the following percentage composition:
The disc was quenched from 1250" C. and tempered for 48 hours at 650 C. It was then found to have the following properties:
Tangen- Transtial Radial verse at centre Creep Deformation (percent) under a tensile stress 8 tons/sq. in. at 300 hours at 600 C 0.073 0 078 0.081 Tensile Strength at room temperature (tons/sq. in):
0.1% proof stress 52. 4 51. 6 49. 9 max. stress 62. 9 62.2 60. 0 Elongation (percent) (L=4 /Z) 15. 5 16.0 15.0 Reduction of Area (percent) 42. 9 37. 9 41. 3
We claim:
1. A ferritic alloy steel having high scale resistance and creep resistance up to about 700 C. and having as essential constituents:
Percent Carbon 0.050.S0 Chromium 8.0 17.0 Nitrogen 0.01-0.25 Silicon 0.1 2.0 Manganese 0.1 4.0
a substance selected from the group consisting of molybdenum (not greater than 4%), tungsten (not greater than 2%) and molybdenum tungsten (not greater than 4%), from 0.05 to 4% of at least three face centered cubic carbide formers including titanium and selected from the group consisting of titanium, vanadium, niobium, tantalum, hafnium, and zirconium, and the remainder being essentially iron.
2. A ferritic alloy steel according to claim 1 containing also any one or more of the following:
Percent Nickel 2.0 Boron O.5 Cobalt Copper 20 3. A ferritic steel alloy having the percentage composition:
And unavoidable impurities.
4. A ferritic alloy steel containing 0.05-0.50% carbon, 8.0-17.0% chromium, a substance selected from the group consisting of molybdenum (not greater than 4%),
5 tungsten (not greater than 2%) and molybdenum tungsten (not greater than 4%), from 0.05 to 4% of at least three face centered cubic carbide formers including titanium and selected from the group consisting of titanium, vanadium, niobium, tantalum, hafnium, and zirconium, the balance substantially iron.
References Cited in the file of this patent UNITED STATES PATENTS Urban Feb. 20, 1951 Krainer Nov. 27, 1951 Kirkby et a1. Apr. 1, 1952
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB2793113X | 1952-08-22 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US2793113A true US2793113A (en) | 1957-05-21 |
Family
ID=10915434
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US375562A Expired - Lifetime US2793113A (en) | 1952-08-22 | 1953-08-20 | Creep resistant steel |
Country Status (1)
| Country | Link |
|---|---|
| US (1) | US2793113A (en) |
Cited By (22)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2854331A (en) * | 1956-10-26 | 1958-09-30 | Latrobe Steel Co | Alloys and alloy articles |
| US2905577A (en) * | 1956-01-05 | 1959-09-22 | Birmingham Small Arms Co Ltd | Creep resistant chromium steel |
| US3069257A (en) * | 1960-06-02 | 1962-12-18 | Armco Steel Corp | Alloy steel and method |
| US3183080A (en) * | 1961-11-21 | 1965-05-11 | Universal Cyclops Steel Corp | Stainless steels and products thereof |
| US3389991A (en) * | 1964-12-23 | 1968-06-25 | Armco Steel Corp | Stainless steel and method |
| US3607239A (en) * | 1967-11-10 | 1971-09-21 | Nippon Kokan Kk | Austenitic heat resisting steel |
| US3663208A (en) * | 1968-06-20 | 1972-05-16 | Firth Brown Ltd | A chromium-nickel alloy steel containing copper |
| US3751244A (en) * | 1970-12-14 | 1973-08-07 | Gijutsa Kenkyushon Nippon Koka | Austenitic heat resisting steel |
| US3767390A (en) * | 1972-02-01 | 1973-10-23 | Allegheny Ludlum Ind Inc | Martensitic stainless steel for high temperature applications |
| US3942954A (en) * | 1970-01-05 | 1976-03-09 | Deutsche Edelstahlwerke Aktiengesellschaft | Sintering steel-bonded carbide hard alloy |
| US4010049A (en) * | 1975-10-06 | 1977-03-01 | Jones & Laughlin Steel Corporation | Columbium-stabilized high chromium ferritic stainless steels containing zirconium |
| US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
| US4059440A (en) * | 1975-02-01 | 1977-11-22 | Nippon Steel Corporation | Highly corrosion resistant ferritic stainless steel |
| FR2491499A1 (en) * | 1980-10-06 | 1982-04-09 | Western Electric Co | ANISOTROPIC MAGNETIC ALLOY AND PROCESS FOR PRODUCING THE SAME |
| US4622067A (en) * | 1985-02-07 | 1986-11-11 | The United States Of America As Represented By The United States Department Of Energy | Low activation ferritic alloys |
| US5207843A (en) * | 1991-07-31 | 1993-05-04 | Latrobe Steel Company | Chromium hot work steel |
| US5310431A (en) * | 1992-10-07 | 1994-05-10 | Robert F. Buck | Creep resistant, precipitation-dispersion-strengthened, martensitic stainless steel and method thereof |
| US5674449A (en) * | 1995-05-25 | 1997-10-07 | Winsert, Inc. | Iron base alloys for internal combustion engine valve seat inserts, and the like |
| US20040154706A1 (en) * | 2003-02-07 | 2004-08-12 | Buck Robert F. | Fine-grained martensitic stainless steel and method thereof |
| US20040154707A1 (en) * | 2003-02-07 | 2004-08-12 | Buck Robert F. | Fine-grained martensitic stainless steel and method thereof |
| US20060283526A1 (en) * | 2004-07-08 | 2006-12-21 | Xuecheng Liang | Wear resistant alloy for valve seat insert used in internal combustion engines |
| CN103534458A (en) * | 2011-06-07 | 2014-01-22 | 博格华纳公司 | Turbocharger and component therefor |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2542220A (en) * | 1948-10-05 | 1951-02-20 | Nat Lead Co | Ferritic alloy |
| US2576229A (en) * | 1941-03-12 | 1951-11-27 | Boehler & Co Ag Geb | Steel for tools operating at elevated temperatures |
| US2590835A (en) * | 1948-12-16 | 1952-04-01 | Firth Vickers Stainless Steels Ltd | Alloy steels |
-
1953
- 1953-08-20 US US375562A patent/US2793113A/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2576229A (en) * | 1941-03-12 | 1951-11-27 | Boehler & Co Ag Geb | Steel for tools operating at elevated temperatures |
| US2542220A (en) * | 1948-10-05 | 1951-02-20 | Nat Lead Co | Ferritic alloy |
| US2590835A (en) * | 1948-12-16 | 1952-04-01 | Firth Vickers Stainless Steels Ltd | Alloy steels |
Cited By (26)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2905577A (en) * | 1956-01-05 | 1959-09-22 | Birmingham Small Arms Co Ltd | Creep resistant chromium steel |
| US2854331A (en) * | 1956-10-26 | 1958-09-30 | Latrobe Steel Co | Alloys and alloy articles |
| US3069257A (en) * | 1960-06-02 | 1962-12-18 | Armco Steel Corp | Alloy steel and method |
| US3183080A (en) * | 1961-11-21 | 1965-05-11 | Universal Cyclops Steel Corp | Stainless steels and products thereof |
| US3389991A (en) * | 1964-12-23 | 1968-06-25 | Armco Steel Corp | Stainless steel and method |
| US3607239A (en) * | 1967-11-10 | 1971-09-21 | Nippon Kokan Kk | Austenitic heat resisting steel |
| US3663208A (en) * | 1968-06-20 | 1972-05-16 | Firth Brown Ltd | A chromium-nickel alloy steel containing copper |
| US3942954A (en) * | 1970-01-05 | 1976-03-09 | Deutsche Edelstahlwerke Aktiengesellschaft | Sintering steel-bonded carbide hard alloy |
| US3751244A (en) * | 1970-12-14 | 1973-08-07 | Gijutsa Kenkyushon Nippon Koka | Austenitic heat resisting steel |
| US3767390A (en) * | 1972-02-01 | 1973-10-23 | Allegheny Ludlum Ind Inc | Martensitic stainless steel for high temperature applications |
| US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
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