CA1103068A - Iron based alloys for machine components subject to mechanical vibration - Google Patents
Iron based alloys for machine components subject to mechanical vibrationInfo
- Publication number
- CA1103068A CA1103068A CA296,940A CA296940A CA1103068A CA 1103068 A CA1103068 A CA 1103068A CA 296940 A CA296940 A CA 296940A CA 1103068 A CA1103068 A CA 1103068A
- Authority
- CA
- Canada
- Prior art keywords
- component
- mechanical vibration
- subject
- maximum
- machine components
- 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
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
- C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
A B S T R A C t A machine component, e.g. a rotary component such as a turbine blade, which is subject to mechanical vibration in use, is made of an alloy containing 5 to 25 wt.% Cr;
maximum 5 wt.% Ti; zero to 5 wt.% Mo; and optionally, maximum 4 vol.% (each) of at least one of the oxides TiO2, Y2O3, MgO, and Al2O3; the balance being Fe and impurities.
maximum 5 wt.% Ti; zero to 5 wt.% Mo; and optionally, maximum 4 vol.% (each) of at least one of the oxides TiO2, Y2O3, MgO, and Al2O3; the balance being Fe and impurities.
Description
1~3~
~he present învention rela-tes to alloys suitable for the manufacture of machine components subject to mechanical-vibration, especially those components which are subject to mechanical vibrations at high temperature, such as gas turbine blades and other rotar~ components.
It is kno~n that, for the above-mentioned purposes, use must be made of alloys having internal damping properties, great strength, and good ductility at temperatures which may reach 700 a or even higher sometimes In particular this is the case when it is desired to ensure a sufficiently long life for the first rows of blades in turbines, which are subjected -to particularly severe mechanical vibrations at high temperature.
In numerous applications 7 especially those in which materials are subjected to mechanical vibrations, the damping capacity of a material may be more important than other properties such as the fatigue limi-t. The da~ping capacity of a material is actually due -to four factors, i.e. plastic deformation, the thermo-elastic ef~ect, the magneto-elastic effect, and atomic diffusion~ ~he ma~neto-electric effect is su-rely the most important in the casè
of alloys designed to be used in industry. It is well recognized that ferromagnetic alloys have, for a number of purposes, better properties than non-magnetic alloys. It has been found that the high damping capacity of ferromagnetic alloys is due to a magneto-mechanical hysteresis effect.
~he energ~ dissipated during a -tensile stress deformation .
) ~3~
cycle because o~ -the magneto-mech~ical ef~ect is responsi-ble for the d~mping capacity of the material.
A material having a high damping capacity is thus a magnetic material having as high as possible a C~rie temperature, while a compromise must be found be-tween the various properties required, i.e. strength at working temperature, damping capacity, oxidation resistance, and - duc-tility at ambient temperature.
In view of the above considerations, a number of industrial materials such as, on the one hand, steels of -the AISI 403 type (12~ Cr) and the AISI 422 type (12% Cr Mo W V~
type and, on the o-ther hand, cobalt-nickel alloys termed NiVCo, and the 70% Mn 30% Cu alloy, have become generally adopted, especially in the manufacture of turbine blades.
~ne choice of alloying elements capable of hardening the ! ferromagne-tic matrices is practically limited, because the various additions have in general the effec-t of lowering the aurie point of an alloy and -thus the damping capacity of the ma-terial.
~or one reason or another, these alloys have dis-advantages which limit the possibility of using them in the above-mentioned applications. Among -these disadvantages one should mention insu~flcient resistance to creep at high temperature, manufacturing difficulties in assembly due to hardness or to fragility or to indeformability, decrease in damping capacity under high dynamic and static stresses, and high cost.
~ 3~
~he present inven-tion concerns an alloy particularly suitable for -the above-mentiorled applications, and in general for machine components which are subject, in use, to more or less severe vibrations due to high speed of rota-tion, to al-tern.a-ting movements, or to speed variations.
~his a]loy is characterized by a composition, by weight, meeting the following relationships:
5% ~- ar ~ 25%
~ 5%
o G~ Mo ~ 5%
the ba.lance being Fe and its usual impurities~ Preferably, the ~i content is at least 0.05 wt %.
It has been found that the above ma-terial simultaneously exhibits good proper-ties of high-temperature strength, ductility, creep resistance, and internal da;~ping, up to temperatures of the order of 700C.
~he invention will be described further, by way of example only, with reference to -the accompanying drawings, in which:
~igure 1 is a graph o.E in.ternal damping verses dynamic strain, at 0.5 Hz, for a component made of a conventional alloy, at various static stresses, ~igure 2 is a graph similar to Fig.ure 1, for a component according to the invention, at various sta-tic stresses;
Figure 3 is a graph of internal damping, at 0.5 Hz, versus ageing temperature, for a component according to the invention subjected to di.fferent heat treatments;
- . :
~3~
Figure 4 is a graph simila- to Figure 2, for R
component according to the invention, at various static stresses; and Figure 5 is a graph similar -to Figure 1, for components made of various alloys.
~he various compositions of the alloys referred to below and in the graphs are given in the following ~able, together with the thermo-mechanical treatment (if any) given to the alloy.
~ABLE
. _ . .. .. .
Alloy Fe Cr Ni Mo Ii ~iO2 ------_______ /o /0 /0 / / 0/
________________________________________________~__________ AISI 410 balance - 13 -- - -- --AI~I 316 ~ 16 13 1 -- __ B 3 E* " 13 ~~ 1.5 2-5 -816** " 13 __ 1.5 3.5 -5 817** " 13 _- 1.5 3-5. 1.0 818** " 13 -- 1.5 3-5 1.5 819** " 13 -- 1.5 3-5 2.0 * extrusion at 1100C
~* extrusion at 1100C, reduction at 1050-1100 C from 19 to 10 mm reduction at 25C from 10 to 8~6 mm heat treatment: 1 hour under argon at 1050 0 .. . .
By way of comparison, Figures 1 and 2 show, at 0.5Hz, the in-ternal damping (in terms of the logarithmic decrement ~ ) as a function of the dynamic strain Y at various static ..
--~\
~ 3~
stresses at roo~ temperature. ~igure 1 relates to the conven-tional AISI ~10 steel whose co~posi-tion is se-t forth in the above ~able, while ~igure 2 relates to an alloy designated B3E whose composition is also given in -the ~able.
By heat treating the allo~ in question, it is possible to modify the shape of tne dam~ing versus strain curve by either varylng the maximum damping value of the corresponding tension. By ageing and solution heat -treatment it is possible to adjust the damping capacity of the allo~, a~ illustrated in Fi~ure 3 ~fter various thermo-mechanical treatments. Hardening of the metal matrix, no longer based on the formation of carbides bu-t on precipitation of a X (chi) phase of the Fe17 Cr17 (~i, Mo)5 type facilitates the use of the alloy at a temperature of 700 a owing to the stabili-ty of the precipitated phase. In ~igure 3, internal damping at 0.5 Hz at a static stress ~ of 20 ~m 2 at room temperature is plotted against ageing temper~ture for the alloy B3E extruded at 1100a ~d then soaked for varl~us tlmes a-t the ageing temperature.
~urthermore, ~igure 4 illustrates the internal damping capacity at 0.5 Hz as a function of the dynamic strain at various levels of the static loads (M~m 2) applied, for the alloy designated 817 in the above ~able, which: is a dispersion-strengthened ferritic steel. ~his graph shows particularly high damPing values under large dynamic stresses, and small da~ping sensitivity with respect to the static load applied, which cons-titutes a further advan-tage.
!
~1~3(~6~3 Figure 5 shows how the values of in-ternal d~mping vary as a function of the composition of the alloy, a-t a single level (high le-vel) of static load ( ~) of 220 l'lNm 2 ~his graph also indicates the damping curve corresponding to the conventional aus-tenitic alloy AISI 31~A One can no-te the large difference between this curve and the curves corresponding to -the other allo-ys, among w~ich tha-t indicated by 81~ is particularly interesting.
According to a variant of the invention and as illustrated in Figures 4 and 5, it has been found -that it is posslble to improve the properties of the alloy by incorporation of a finely dispersed inert phase in the matri~ and by taking advantage of the possibilities of powder metallurgy. According to a preferred composition, the addition of one or more of the following oxides -to the metal matrix, ia -the indicated proportions, was found to be particularly satisfac-tory:
~i2 ~ 4% by volume Y203 ~ 4% by volume Mg70 ~- 4% by volume A1203 ~- 4% by volume.
~he present învention rela-tes to alloys suitable for the manufacture of machine components subject to mechanical-vibration, especially those components which are subject to mechanical vibrations at high temperature, such as gas turbine blades and other rotar~ components.
It is kno~n that, for the above-mentioned purposes, use must be made of alloys having internal damping properties, great strength, and good ductility at temperatures which may reach 700 a or even higher sometimes In particular this is the case when it is desired to ensure a sufficiently long life for the first rows of blades in turbines, which are subjected -to particularly severe mechanical vibrations at high temperature.
In numerous applications 7 especially those in which materials are subjected to mechanical vibrations, the damping capacity of a material may be more important than other properties such as the fatigue limi-t. The da~ping capacity of a material is actually due -to four factors, i.e. plastic deformation, the thermo-elastic ef~ect, the magneto-elastic effect, and atomic diffusion~ ~he ma~neto-electric effect is su-rely the most important in the casè
of alloys designed to be used in industry. It is well recognized that ferromagnetic alloys have, for a number of purposes, better properties than non-magnetic alloys. It has been found that the high damping capacity of ferromagnetic alloys is due to a magneto-mechanical hysteresis effect.
~he energ~ dissipated during a -tensile stress deformation .
) ~3~
cycle because o~ -the magneto-mech~ical ef~ect is responsi-ble for the d~mping capacity of the material.
A material having a high damping capacity is thus a magnetic material having as high as possible a C~rie temperature, while a compromise must be found be-tween the various properties required, i.e. strength at working temperature, damping capacity, oxidation resistance, and - duc-tility at ambient temperature.
In view of the above considerations, a number of industrial materials such as, on the one hand, steels of -the AISI 403 type (12~ Cr) and the AISI 422 type (12% Cr Mo W V~
type and, on the o-ther hand, cobalt-nickel alloys termed NiVCo, and the 70% Mn 30% Cu alloy, have become generally adopted, especially in the manufacture of turbine blades.
~ne choice of alloying elements capable of hardening the ! ferromagne-tic matrices is practically limited, because the various additions have in general the effec-t of lowering the aurie point of an alloy and -thus the damping capacity of the ma-terial.
~or one reason or another, these alloys have dis-advantages which limit the possibility of using them in the above-mentioned applications. Among -these disadvantages one should mention insu~flcient resistance to creep at high temperature, manufacturing difficulties in assembly due to hardness or to fragility or to indeformability, decrease in damping capacity under high dynamic and static stresses, and high cost.
~ 3~
~he present inven-tion concerns an alloy particularly suitable for -the above-mentiorled applications, and in general for machine components which are subject, in use, to more or less severe vibrations due to high speed of rota-tion, to al-tern.a-ting movements, or to speed variations.
~his a]loy is characterized by a composition, by weight, meeting the following relationships:
5% ~- ar ~ 25%
~ 5%
o G~ Mo ~ 5%
the ba.lance being Fe and its usual impurities~ Preferably, the ~i content is at least 0.05 wt %.
It has been found that the above ma-terial simultaneously exhibits good proper-ties of high-temperature strength, ductility, creep resistance, and internal da;~ping, up to temperatures of the order of 700C.
~he invention will be described further, by way of example only, with reference to -the accompanying drawings, in which:
~igure 1 is a graph o.E in.ternal damping verses dynamic strain, at 0.5 Hz, for a component made of a conventional alloy, at various static stresses, ~igure 2 is a graph similar to Fig.ure 1, for a component according to the invention, at various sta-tic stresses;
Figure 3 is a graph of internal damping, at 0.5 Hz, versus ageing temperature, for a component according to the invention subjected to di.fferent heat treatments;
- . :
~3~
Figure 4 is a graph simila- to Figure 2, for R
component according to the invention, at various static stresses; and Figure 5 is a graph similar -to Figure 1, for components made of various alloys.
~he various compositions of the alloys referred to below and in the graphs are given in the following ~able, together with the thermo-mechanical treatment (if any) given to the alloy.
~ABLE
. _ . .. .. .
Alloy Fe Cr Ni Mo Ii ~iO2 ------_______ /o /0 /0 / / 0/
________________________________________________~__________ AISI 410 balance - 13 -- - -- --AI~I 316 ~ 16 13 1 -- __ B 3 E* " 13 ~~ 1.5 2-5 -816** " 13 __ 1.5 3.5 -5 817** " 13 _- 1.5 3-5. 1.0 818** " 13 -- 1.5 3-5 1.5 819** " 13 -- 1.5 3-5 2.0 * extrusion at 1100C
~* extrusion at 1100C, reduction at 1050-1100 C from 19 to 10 mm reduction at 25C from 10 to 8~6 mm heat treatment: 1 hour under argon at 1050 0 .. . .
By way of comparison, Figures 1 and 2 show, at 0.5Hz, the in-ternal damping (in terms of the logarithmic decrement ~ ) as a function of the dynamic strain Y at various static ..
--~\
~ 3~
stresses at roo~ temperature. ~igure 1 relates to the conven-tional AISI ~10 steel whose co~posi-tion is se-t forth in the above ~able, while ~igure 2 relates to an alloy designated B3E whose composition is also given in -the ~able.
By heat treating the allo~ in question, it is possible to modify the shape of tne dam~ing versus strain curve by either varylng the maximum damping value of the corresponding tension. By ageing and solution heat -treatment it is possible to adjust the damping capacity of the allo~, a~ illustrated in Fi~ure 3 ~fter various thermo-mechanical treatments. Hardening of the metal matrix, no longer based on the formation of carbides bu-t on precipitation of a X (chi) phase of the Fe17 Cr17 (~i, Mo)5 type facilitates the use of the alloy at a temperature of 700 a owing to the stabili-ty of the precipitated phase. In ~igure 3, internal damping at 0.5 Hz at a static stress ~ of 20 ~m 2 at room temperature is plotted against ageing temper~ture for the alloy B3E extruded at 1100a ~d then soaked for varl~us tlmes a-t the ageing temperature.
~urthermore, ~igure 4 illustrates the internal damping capacity at 0.5 Hz as a function of the dynamic strain at various levels of the static loads (M~m 2) applied, for the alloy designated 817 in the above ~able, which: is a dispersion-strengthened ferritic steel. ~his graph shows particularly high damPing values under large dynamic stresses, and small da~ping sensitivity with respect to the static load applied, which cons-titutes a further advan-tage.
!
~1~3(~6~3 Figure 5 shows how the values of in-ternal d~mping vary as a function of the composition of the alloy, a-t a single level (high le-vel) of static load ( ~) of 220 l'lNm 2 ~his graph also indicates the damping curve corresponding to the conventional aus-tenitic alloy AISI 31~A One can no-te the large difference between this curve and the curves corresponding to -the other allo-ys, among w~ich tha-t indicated by 81~ is particularly interesting.
According to a variant of the invention and as illustrated in Figures 4 and 5, it has been found -that it is posslble to improve the properties of the alloy by incorporation of a finely dispersed inert phase in the matri~ and by taking advantage of the possibilities of powder metallurgy. According to a preferred composition, the addition of one or more of the following oxides -to the metal matrix, ia -the indicated proportions, was found to be particularly satisfac-tory:
~i2 ~ 4% by volume Y203 ~ 4% by volume Mg70 ~- 4% by volume A1203 ~- 4% by volume.
Claims (6)
PROPERTY OR PRIVILEGE IS CLAIMED ARE DEFINED AS FOLLOWS:
1. A machine component which, in use, is subject to mechanical vibration, the component being made of an alloy containing: 5 to 25 wt. % Cr, titanium in an amount up to 5 wt. %
and zero to 5 wt. % Mo, the balance being Fe and impurities.
and zero to 5 wt. % Mo, the balance being Fe and impurities.
2. A component as claimed in claim 1, being a component which, in use, is subject to rotational movement causing mechanical vibration.
3. A component as claimed in claim 2, being a turbine blade.
4. A machine component which, in use, is subject to mechanical vibration, the component being made of an alloy containing: 5 to 25 wt. % Cr; titanium in an amount up to 5 wt. %;
zero to 5 wt. % Mo; and at least one oxide selected from the group consisting of maximum 4 vol. % TiO2, maximum 4 vol. % Y2O3, maximum 4 vol. % MgO, and maximum 4 vol. % Al2O3, the balance being Fe and impurities.
zero to 5 wt. % Mo; and at least one oxide selected from the group consisting of maximum 4 vol. % TiO2, maximum 4 vol. % Y2O3, maximum 4 vol. % MgO, and maximum 4 vol. % Al2O3, the balance being Fe and impurities.
5. A component as claimed in claim 4, being a component which, in use, is subject to rotational movement causing mechanical vibration.
6. A component as claimed in claim 5, being a turbine blade.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| BE851449 | 1977-02-15 | ||
| BE851.449 | 1977-02-15 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1103068A true CA1103068A (en) | 1981-06-16 |
Family
ID=3861483
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA296,940A Expired CA1103068A (en) | 1977-02-15 | 1978-02-14 | Iron based alloys for machine components subject to mechanical vibration |
Country Status (6)
| Country | Link |
|---|---|
| JP (1) | JPS53100912A (en) |
| CA (1) | CA1103068A (en) |
| FR (1) | FR2380349A1 (en) |
| IT (1) | IT1107068B (en) |
| NL (1) | NL7801634A (en) |
| SE (1) | SE439497B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103602906B (en) * | 2013-11-18 | 2015-04-08 | 山东聊城莱鑫超硬材料有限公司 | Heating element for synthesizing diamond |
-
1978
- 1978-02-10 SE SE7801588A patent/SE439497B/en not_active IP Right Cessation
- 1978-02-10 IT IT67267/78A patent/IT1107068B/en active
- 1978-02-14 CA CA296,940A patent/CA1103068A/en not_active Expired
- 1978-02-14 NL NL7801634A patent/NL7801634A/en not_active Application Discontinuation
- 1978-02-15 FR FR7804988A patent/FR2380349A1/en active Granted
- 1978-02-15 JP JP1638978A patent/JPS53100912A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| FR2380349B1 (en) | 1984-04-20 |
| JPS53100912A (en) | 1978-09-02 |
| IT1107068B (en) | 1985-11-18 |
| IT7867267A0 (en) | 1978-02-10 |
| FR2380349A1 (en) | 1978-09-08 |
| SE439497B (en) | 1985-06-17 |
| SE7801588L (en) | 1978-08-15 |
| NL7801634A (en) | 1978-08-17 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MKEX | Expiry |