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Mo-V-Ni high temperature steels, articles made therefrom and method of making

Inactive Publication Date: 2008-06-19
THE TIMKEN CO
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  • Summary
  • Abstract
  • Description
  • Claims
  • Application Information

AI Technical Summary

Benefits of technology

[0029]Providing an alloy consisting essentially of in % by weight less than 1.25% Cr, preferably 0.75% to 1.25% Cr, about: 0.40% Mn≦4%, 0≦Mo≦4.00, preferably 1.0% to 3.00% Mo, 0%≦V≦2.0%, preferably 0.75% to 1.25% V, 1.0%≦Ni≦3.0%, less than 0.20% Si, a carbon content selected from one of about 0.05%≦C≦0.40% defining a carburizing steel or 0.40%<C≦1.25% defining a high carbon steel, and the balance iron plus incidental impurities. Tungsten (W) is not purposely added to these alloys. The amount of tungsten is ideally zero, or as low as commercially feasible and practical, preferably no more than 0.20% W. In general, the total amount of (Mo+V) will be less than 4% and the amount of (Mo+V+Ni+Cr) will preferably be 4% to 8%. The uniqueness of these alloys is that they achieve excellent hot hardness with a minimum of the recited alloy additions, and contain manganese (Mn) to enhance carbon diffusion and increase hardenability. This is unlike normal high speed steels that achieve good hot hardness with large amounts of alloying elements. Elements such as nitrogen (N), niobium (Nb) or even titanium (Ti) and other similar elements may be added in small amounts up to about 0.05% each for grain refinement and enhanced toughness purposes.

Problems solved by technology

First, low melting point alloy carbides do not form in the steels, particularly the steels containing 1% carbon.

Method used

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  • Mo-V-Ni high temperature steels, articles made therefrom and method of making
  • Mo-V-Ni high temperature steels, articles made therefrom and method of making
  • Mo-V-Ni high temperature steels, articles made therefrom and method of making

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example 1

Preliminary Studies

[0073]The initial research pertaining to the present invention examined several alloy steels presently used in various applications and determined how they could be carburized with respect to a laboratory alloy containing just 0.20% carbon and the balance iron. Specimens of the iron −0.20% C alloy (Heat 2128) and laboratory heats of 8119 (Heat 2132), CBS 400 (Heat 2124) and CBS 600 (Heat 2126) were carburized using normal production cycles, Table 3. As indicated by measuring the carbon content of the specimens at different depths, the results for 8119 and the 0.20% carbon alloy (Heat 2128) were similar, FIG. 5. However, the CBS 400 and CBS 600 alloys did not contain as much carbon per test depth as the specimen without alloy additions. This suggests that the various combinations of the alloy constituents present in CBS 600 and CBS 400 actually impede the diffusion of carbon into the specimens. Another group of specimens were carburized at the same time as these sp...

example 2

Series 1—Room Temperature Design Matrix; 1% Carbon and Carburized 0.2% C Alloys

[0078]The first design matrix, referred to as Series 1, used for alloy development was composed of the following elements: Approximately 1% Cr was included in each laboratory alloy. Chromium increases the hardenability of alloy steels, and at the 1% level, it has been shown not to be detrimental to the carburizing process. Approximately 0.40% Mn was included in each alloy. This level was chosen for the improvement in hardenability given by Mn and by its enhancement of the carburizing process. However, the level of Mn was not made larger because, as mentioned above, Mn does not significantly improve the hot hardness of alloy steels. Less than 0.20% Si was included in the experimental steels so as to avoid detrimental effects on carbon diffusion in austenite. A low silicon content was also desirable in preventing the formation of low melting point carbides in the test alloys. Various amounts of Mo, V and Ni...

example 3

Series 2 and 3—Room Temperature Design Matrix; 1% Carbon and Carburized 0.2% C Alloys

[0079]Based on the results obtained from the alloys in Series 1, two additional groups of alloys were melted, processed and evaluated. As with Series 1, the additional heats of steel (Series 2) were split into two groups. For the steels of Series 2, the nominal carbon contents were 1.25% (through hardening) and 0.20% (carburizing). The molybdenum content of these steels ranged from 2.9% through 6.8%, Tables 6 and 7. For the steels of Series 3, the nominal carbon contents were 1.0% (through hardening) and 0.20% (carburizing), and the nominal molybdenum content was 3%. The vanadium content of these alloys ranged from 0% through 1%, and the Ni content ranged from 1% through 3%, Tables 8 and 9.

TABLE 6Composition and room temperature hardness of Series 2 throughhardened steels. For all heats, Cr ≈ 1.0%, V ≈ 1.0%, Mn ≈ 0.40% andSi ≈ 0.12%.Composition (wt. %)Hardness (HK)HeatCMoVNiγ830° C.*γ1190° C.**24691...

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Abstract

Low carbon carburizing (surface hardening) and higher carbon through hardening steels primarily containing molybdenum, vanadium and nickel and, to a lesser amount, chromium used for rolling contact bearings, gears and other similar applications where high hardness at elevated temperatures is required. The alloy steel includes, in % by weight: 0.05% to 1.25% C; up to 1.25% Cr; 0.40% to 4% Mn; up to 4.0% Mo; up to 2.0% V; 1.0% to 3.0% Ni; 4% to 8% (Mo+V+Ni+Cr); less than 0.20% Si; and balance Fe plus incidental additions and impurities. The method for providing a steel having improved hardness at elevated temperatures includes the steps of: (a) providing an alloy including, in % by weight: less than 1.25% Cr, 0.4% to 4% Mn, up to 4% Mo, up to 2% V, 1 to 3% Ni, 4% to 8% (Mo+V+Ni+Cr), less than 0.2% Si, a C content selected from one of 0.05% to 0.40% C defining a carburizing steel or greater than 0.40% to 1.25% C defining a through hardening steel, and the balance Fe plus incidental additions and impurities; (b) performing a step selected from the group consisting of (i) subjecting the carburizing steel to carburizing and quenching to provide a quenched carburized steel, or (ii) subjecting the high carbon steel to hot working to provide a wrought high carbon steel; (c) preheating the quenched carburized steel or wrought high carbon steel and then austenitizing said steel to provide an austenitized steel; (d)quenching the austenitized steel to provide quenched austenitized steel; and (e) tempering the quenched austenitized steel followed by air cooling.

Description

BACKGROUND OF THE INVENTION[0001]1. Field of the Invention[0002]The present invention relates to both low carbon carburizing (surface hardening) and higher carbon through hardening steels primarily containing molybdenum, vanadium and nickel and, to a lesser amount, chromium used for rolling contact bearings, gears and other similar applications where high hardness at elevated temperatures is required.[0003]2. Description of Related Art[0004]Piston driven aircraft engines and early jet engines used through hardening 52100 alloy steel or carburizing grades of alloy steels for most bearing applications, see Table 1. However, over the years, as power requirements rose, operating temperatures increased. Thus, alloys with more heat resistance were necessary. Minor improvements in the performance of 52100 alloy steel were achieved by adding small amounts of extra alloying elements. One of the most commonly added elements to enhance high temperature performance was silicon. TSB-600 is a typ...

Claims

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Application Information

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IPC IPC(8): C22C38/46C22C38/22C23C8/22C21D5/00C21D8/00C22C38/44
CPCC21D5/00C23C8/80C23C8/22C21D8/00
Inventor HETZNER, DENNIS W.WAID, GEORGE M.
Owner THE TIMKEN CO
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