CA2104607C - Sintered coining process - Google Patents
Sintered coining processInfo
- Publication number
- CA2104607C CA2104607C CA 2104607 CA2104607A CA2104607C CA 2104607 C CA2104607 C CA 2104607C CA 2104607 CA2104607 CA 2104607 CA 2104607 A CA2104607 A CA 2104607A CA 2104607 C CA2104607 C CA 2104607C
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- CA
- Canada
- Prior art keywords
- sintered
- articles
- coining
- ferro
- manganese
- 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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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
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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)
Abstract
A process of coining sintered articles of powder metal comprising: blending carb on, ferro manganese, and lubricant with compressible elemental iron powder, pressing the blended mixture to form the articles, high temperature sintering of the articles in a reducing atmosphere and then coining the sintered articles to final shape so as to narrow the tolerance variability of coined articles and substantially eliminate secondary operations.
Description
PCT / ~A 9 2 / U 0 5 5 210g607 AS SINTERED COINING PROCESS
FIELD OF INVENIION
This invention relates to a process of coining sintered articles to final shape and in particular relates to a process of precision coining sintered articles of powder metal having a composition of between 0.3% to 2.0~ m~ng~nese, 0.2 to 0.85% carbon withthe rem~inder being iron and unavoidable impurities where the sintered articles are coined to final shape so as to narrow the tolerance variability of the coined articles.
Background to the Invention Powder metal technology is well known to the persons skilled in the art and generally comprises the formation of metal powders which are compacted and then subjected to an elevated temperature so as to produce a sintered product.
Conventional sintering occurs at a m~xi~ temperature of approximately up to 1,150 ~ C. Historically the upper temperature has been limited to this temperature by sintering equipment availability. Therefore copper and nickel have traditionally been used as alloying additions when sintering has been conducted at conventional temperatures of up to 1,150~ C, as their oxides are easily reduced at these temperatures in a generated atmosphere, of relatively high dew point cont~ining CO, CO2 and H2. The use of copper and nickel as an alloying material is expensive.
Moreover, copper when utilized in combination with carbon as an alloying material and sintered at high temperatures causes dimensional instability and accordingly the use of same in a high temperature sintering process results in a more difficult process to control the dimensional characteristics of the desired product.
M~nllf~ctllrers of metal powders utilized in powder metal technology produce prealloyed iron powders which are generally more difficult to compact into complex shapes, particularly at higher densities (> 7.0 g/cc). Manganese and chromium can be incorporated into prealloyed powders provided special m~nl~f~cturing precautions are taken to ~ e the oxygen content, for example, by oil atornization.
21046Q7 pc~ / ~A 9 2 / ~ 0 5 5 5 "
FIELD OF INVENIION
This invention relates to a process of coining sintered articles to final shape and in particular relates to a process of precision coining sintered articles of powder metal having a composition of between 0.3% to 2.0~ m~ng~nese, 0.2 to 0.85% carbon withthe rem~inder being iron and unavoidable impurities where the sintered articles are coined to final shape so as to narrow the tolerance variability of the coined articles.
Background to the Invention Powder metal technology is well known to the persons skilled in the art and generally comprises the formation of metal powders which are compacted and then subjected to an elevated temperature so as to produce a sintered product.
Conventional sintering occurs at a m~xi~ temperature of approximately up to 1,150 ~ C. Historically the upper temperature has been limited to this temperature by sintering equipment availability. Therefore copper and nickel have traditionally been used as alloying additions when sintering has been conducted at conventional temperatures of up to 1,150~ C, as their oxides are easily reduced at these temperatures in a generated atmosphere, of relatively high dew point cont~ining CO, CO2 and H2. The use of copper and nickel as an alloying material is expensive.
Moreover, copper when utilized in combination with carbon as an alloying material and sintered at high temperatures causes dimensional instability and accordingly the use of same in a high temperature sintering process results in a more difficult process to control the dimensional characteristics of the desired product.
M~nllf~ctllrers of metal powders utilized in powder metal technology produce prealloyed iron powders which are generally more difficult to compact into complex shapes, particularly at higher densities (> 7.0 g/cc). Manganese and chromium can be incorporated into prealloyed powders provided special m~nl~f~cturing precautions are taken to ~ e the oxygen content, for example, by oil atornization.
21046Q7 pc~ / ~A 9 2 / ~ 0 5 5 5 "
Notwithst:~n~ling this, these powders still have poor compressabilities compared to admixed powders.
Conventional means to increase the strength of powder metal articles use up to 8~c nickel, 4% copper and 1.5~o molybdenum, in prealloyed, partially prealloyed, or admixed powders. Furthermore double press double sintering can be used for high performance parts as a means of increasing part density. Conventional elements are expensive and relatively ineffective for generating mechanical properties equivalent to wrought steel products, which comrnonly use the more effective strengthening alloying elements m~ng~nese and chro~
Moreover, conventional technology as disclosed in United States Patent No. 2,402,120 teach pulverizing material such as mill scale to a very fine sized powder, and thereafter reducing the mill scale powder to iron powder without melting it.
Furtherrnore, United States Patent No. 2,289,569 relates generally to powder metallurgy and more particularly to a low melting point alloy powder and to the usage of the low melting point alloy powders in the formation of sintered articles.
Yet another process is disclosed in United States Patent No. 2,027,763 which relates to a process of m~kinE sintered hard metal and consists essentially of steps cormected with the process in the production of hard metal. In particular, United States Patent No. 2,027,763 relates to a process of m~king sintered hard metal which comprisesproducing a spray of dry, finely powdered mixture of fusible metals and a readily fusible ~lxili~ry metal under high pressure producing a spray of adhesive agent customary for binding hard metals under high stress, and so directing the sprays that the spray of metallic powder and the spray of adhesive liquid will meet on their way tn the molds! or within the latter, whereby the mold will become filled with a compact moist mass of metallic powder and finally completing the hard metallic particle thus formed by sintering.
United States Patent No.4,707,332 teaches a process for m~n~lf~cturing structural parts from intermetallic phases capable of sintering by means of special additives which serve at the same time as sintering assists and increase the ductility of the finished structural product.
Moreover, United States Patent No. 4,464,206 relates to a wrought powder metal process for pre-alloyed powder. In particular, United States Patent No. 4,464,206 teaches a process comprising the steps of commllnim~ting substantially non-compactible pre-alloyed metal powders so as to flatten the particles thereof heating the commllninllted particles of metal powder at an elevated temperature, with the particles adhering and forming a mass during heating, crushing the mass of metal powder, compacting the crushed mass of metal powder, sintering the metal powder and hot working the metal powder into a wrought product.
Finally, Goining is a process well known to those persons skilled in the art. However, a comprehensive method of precision coining of powder metal blanks is lacking. For example, United States Patent No. 2,757,446 teaches a method of forming articles from metal powders which includes hot forging the article to a minimum density of 95 % of the theoretical density wherein the entire change of shape of the article takes places in one direction of movement and wherein the minimum internal flow of the particleswithin the article is at least 5 % and finally finishing the forged article.
The processes as described in the prior art above present a relatively less cost effective process to achieve the desired mechanical properties of the sintered product.
An aspect of the invention relates to a coining process for blending, sintering, and coining powder metal articles, that coining process comprising: blending carbon, ferro manganese and lubricant with compressible iron powder to form a blended mixture;pressing said blended mixture to form said articles; sintering said articles in a reducing atmosphere at a temperature of at least 1250C; and coining said sintered articles to a final shape.
~ 1 ~ 4 ~ Q 7 It is another aspect of this invention to provide a process of precision coining a sintered article of powder metal comprising: selecting iron powder; determining the desired properties of said sintered article and selecting; a quantity of carbon; and a quantity of ferro manganese to produce an article having a composition of between 0.3% to 2.0%
manganese, 0.2% to 0.85% carbon with the remainder being iron and unavoidable impurities; grinding separately said ferro manganese to a mean particle size of approximately 8 to 12 microns and substantially all of said ferro manganese having a particle size of less than 25 microns; introducing a lubricant while blending said carbon, and ferro manganese with said iron powder; pressing said mixture to form said article; sintering said article at a temperature between 1,250~C and 1,350~C in a vacuum or reducing atmosphere of 90% blended nitrogen and 10% hydrogen to produce said sintered article of powdered metal; coining said sintered article to a final shape to narrow the dimensional tolerance variability of coined articles and substantially elimin~te secondary operations.
It is a further aspect of the invention to provide a process of gas quenching coined articles of powder metal, that process comprising: blending carbon, ferro m~ng~nese, ferro molybdenum, ferro chromium and lubricant with compressible iron powder;
pressing said blended mixture to form said articles; sintering said articles at a temperature in the range of 1250 C to 1350 C in a reducing atmosphere; coining said articles to a final form; and gas quenching said articles.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0. 3 to 2. 5 % manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 - 4a - 2 ~ ~ 4 6 0 7 ....
microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0. 3 to 2 . 5 % manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0.5 to 2.0% manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having 1.5% manganese and .8% carbon composition where said product is machined or coined to final dimensional requirements.
Description of Drawings These and other features and objections of the invention will now be described in relation to the following drawings:
Figure 1 is a drawing of the prior art mixture of iron alloy.
Figure 2 is a drawing of a mixture of elemental iron, and ferro alloy in accordance with the invention described herein.
2104~7 - s .
Figure 3 is a graph showing the distribution of particle size in accordance with the invention herein.
Figure 4 is representative drawing of a jet mill utilized to produce the particle size of the ferro alloy.
Figure S is a stress strain graph.
Figure 6 illustrates a coin~d part such as a clutch backing plate made in accordance with the invention.
Figure 7 is a dimensional stability graph.
Figure 8 graphically illustrates the narrow variability tolerance of the coined parts.
DESCRIP IION OF THE INVENTION
Sintered Powder Metal Method Figure 1 is a representative view of a rni~cture of powder metal utilized in the prior art which consists of particles of ferro alloy in powder metal technology.
In particular, copper and nickel may be used as the alloying materials, particularly if the powder metal is subjected to conventional temperature of up to 1150 ~ C during the sintering process.
Moreover, other alloying materials such as manganese, chromium, and molybdenum which were alloyed with iron could be added by means of a master alloy although such elements were tied together in the prior art. For example a comrnon master alloyconsists of 22% of m~n~nese, 22~o of chromium and 225~o of molybdenum, with the balance consisting of iron and carbon. The utilization of the elements in a tied form made it difficult to tailor the mechanical properties of the final sintered product for specific applications. Also the cost of the master alloy is very high and uneconomic.
By lltili7.ing ferro alloys which consist of ferro m~nganese, or ferro chromium or ferro molybdenum or ferro vanadium, separately from one another rather than l]tili7in~ a ferro alloy which consists of a combination of iron, with manganese, chromium, molybdenum or vanadium tied together a more accurate control on the desired properties of the finished product may be accomplished so as to produce a methodhaving more flexibility than accomplished by the prior art as well as being more cost effective.
Figure 2 is a representative drawing of the invention to be described herein, which consists of iron particles, Fe having a mixture of ferro alloys 2.
The ferro alloy 2 can be selected from the following groups:
Name Symbol Approx. % of Alloy Element ferro manganese FeMn 78%
ferro chromium FeCr 65%
ferro molybdenum FeMo 71%
ferro vanadium FeVa 75%
ferro silicon FeSi 75%
ferro boron FeB 17.5%
The ferro alloys available in the market place may also contain carbon as well as unavoidable impurities which is well known to those people skilled in the art.
Chromium molybdenum and v~n~(lillm are added to increase the strength of the finished product particularly when the product is subjected to heat treatment after sintering. Moreover, manganese is added to increase the strength of the finished product, particularly if one is not heat treating the product after the sintering stage.
The reason for this is manganese is a powerful ferrite strengthener (up to 4 times more effective than nickel).
Particularly good results are achieved in the method described herein by grinding the ferro alloys so as to have a Dso or mean particle size of 8 to 12 microns and a Dloo of up to 25 microns where subst~nti~lly all particles of the ferro alloys are less than 25 microns as shown in Figure 3. For certain application a finer distribution may be desirable. For example a D50 of 4 to 8 microns and a Dloo of 15 microns.
Many of the processes used in the prior art have previously used a D50 of 15 microns as illustrated by the dotted lines of Figure 3. It has been found that by finely grinding the of the ferro alloy to a fine particle size in an inert atmosphere as described herein a better balance of mechanical properties may be achieved having improved sintered pore morphology. In other words the porosity is smaller and more rounded and more evenly distributed throughout the mass which enhances strength characteristics of the finished product. In particular, powder metal products are produced which are much tougher than have been achieved heretofore.
The ferro alloy powders may be ground by a variety of means so long as the mean particle size is between 8 and 12 microns. For example, the ferro alloy powders may be ground in a ball mill, or an attritor, provided precautions are taken to prevent oxidation of the ground particles and to control the grinding to obtain the desired particle size distribution.
Particularly good results in controlling the particle size as described herein are achieved by utili~ing the jet mill illustrated in Figure 4. In particular, an inert gas such as cyclohexane, nitrogen or argon is introduced into the grinding chamber via nozzles 4 which fluidize and impart high energy to the particles of ferro alloys 6 upward and causes the ferro alloy particles to break up against each other. As the ferro alloy particles grind up against each other and reduce in size they are lifted higher up the chamber by the gas flow and into a classifier wheel 10 which is set at a particular RPM. The particles of ferro alloy enter the classifier wheel 10 where the ferro alloy particles which are too big are returned into the chamber 8 for further grinding while particles which are small enough namely those particles of ferro alloy having a particle size of less than 25 microns pass through the wheel 10 and collect in the collecting zone 12. The grinding of the ferro alloy material is conducted in an inert gas atmosphere as described above in order to prevent oxidization of the ferro alloymaterial. Accordingly, the grinding mill shown in Figure 4 is a totally enclosedsystem. The jet mill which is utilized accurately controls the size of the particles which are ground and produces a distribution of ground particles which are narrowly centralized as shown in Figure 3. The classifier wheel speed is set to obtain a D50 of 8 to 10 microns. The speed will vary with different ferro alloys being ground.
The mechanical properties of a produced powder metal product may be accurately controlled by: .
(a) selecting elemental iron powder;
(b) determining the desired properties of the sintered article and selecting:
(i) a quantity of carbon; and (ii) the ferro alloy(s) from the group of ferro manganese, ferro chromium, ferro molybdenum, and ferro vanadium and selecting the quantity of same;
(c) grinding separately the ferro alloy(s) to a mean particle size of approximately 8 to 12 microns, which grinding may take place in a jet mill as described herein;
(d) introducing a lubricant while blending the carbon and ferro alloy(s) with the elemental iron powder;
(e) pressing the mixture to form the article; and (f~ subjecting the article to a high temperature sintering at a temperature of between 1,250 ~ C and 1,350 ~ C in a reducing atmosphere of, for example 90% nitrogen and 10% hydrogen.
The lubricant is added in a manner well known to those persons skilled in the art so as to assist in the binding of the powder as well as assisting in the ejecting of the product after pressing. The article is formed by pressing the mixture into shape by utilizing the appropriate pressure of, for example, 25 to 50 tonnes per square inch.
The invention disclosed herein utilizes high temperature sintering of 1,250~C to1,350~C and a reducing atmosphere of, for example nitrogen and hydrogen in a 90/10% ratio, or in vacuum. Moreover, the reducing atmosphere in combination with the high sintering temperature reduces or cleans off the surface oxides allowing the particles to form good bonds and the compacted article to develop the appl-opliate strength. A higher temperature is lltili7e~l in order to create the low dew point necessary to reduce the oxides of manganese and chromium which are difficult to reduce. The conventional practice of sintering at 1150~C does not create a sintering regime with the right combination of low enough dew point and high enough temperature to reduce the oxides of chromium, manganese, vanadium and silicon.
Secondary operations such as machining or the like may be introduced after the sintering stage. Moreover, heat treating stages may be introduced after the sintering stage.
Advantages have been realized by utili7ing the invention as described herein. For example, manganese, chromium and molybdenum ferro alloys are utili7e~1 to strengthen the iron which in combination or singly are less expensive than the copper and nickel alloys which have heretofore been used in the prior art. Moreover, manganese appears to be four times more effective in strengthening iron than nickel as 1 % of manganese is approximately equivalent to 4% nickel, and accordingly a cost advantage has been realized.
Furthermore sintered steels with molybdenum, chromium, manganese and vanadium are dimensionally more stable during sintering at high temperatures described herein than are iron-copper-carbon steels (ie. conventional powder metal (P/M) steels).Process control is therefore easier and more cost effective than with conventional P/M
alloys.
Furthermore, the microstructure of the finished product are improved as they exhibit:
(a) well rounded pores;
(b) a homogenous structure;
(c) structure having a much smaller grain size; and (d) a product that is more similar to wrought and cast steels in composition than conventional powder metal steels.
The process described herein allows one to control or tailor the materials which are desired for a particular application.
( 1 ) sinter hardening grades (2) gas quenched grades (3) as sintered grades (4) high strength grades (5) high ductility grades The following chart provides examples of the five grades referred to above as well as the range of compositions that may be lltili7e~l in accordance with the procedure outlined herein.
Alloy Type Composition Typical Mechanical Properties Ultimate Tensile Stren~th Im~act UTS (ksi) ~L/Ib As Sintered Mn: 0.3 - 2.5%90 25 C: 0.2 - 0.85%
~CT l CA 9 2 ~ O 0 5 5 5 21Q~607 Sinter Hardening Mn: 1.0 - 2.0% 120 LS
C: 0.5 - 0.85%
Mo: 0 -1.0%
Gas Quenched Mn: 0.5 - 2.0% 150 15 Mo: 0.5- 1.5%
C: 0 - 0.8%
Cr: 0 -1.0%
High Strength Mn: 0.5 - 2.0% 200 8 Cr: 0.5 - 2.0%
Mo: 0 -1.0%
C: 0.1 - 0.6%
High Ductility Cr: 0.5 - 2.0% 80 15 Mo: 0- 1.0%
C: 0.1 - 0.6%
Particularly good results were achieved with the as sintered grade with 1.5% Mn and Q.Q,C'c_; UTS of 90ksi and imp_cL strength of 2û ft lbs. Otlqer C 01-.~inati5nS e~f 2Iloyirg are possible to produce articles with specifically tailored baIance of properties such as high tollghness and ware resistance.
Moreover good results were achieved with:
(a) sinter hardening grade with 1.5% Mn, 0.5% Mo, and 0.850~G C;
(b) gas quenching grade (i) with 1.5% Mn, 0.5% Mo, and 0.5% C
(ii) with 0.5% Cr, 1.0% Mn, and 0.5% C
(c) high strength grade (i) with 1.0% Mn, 0.5% C, 0.5% Cr, 0.5% Mo (ii) with 1.5% Cr, 0.6~o C, 1.0% Mn, Rollable Grade Moreover, the method described herein may be utilized to produce a sixth grade identified as a rollable grade having the following composition:
PC~ 1 ~A 9, i 0 0 5 5 5 210~6~7 Rollable Grade Cr: O.S - 2.0% 80 15 Mo: 0- 1.0C~o C: 0.1 - 0.6%
Mn: 0 to 0.6~c Coinin~
., It has been found that the method of producing the as sintered grade as described above is particularly useful when used in combination with a coining operation so as to produce precision coining as sintered parts which substantially elimin~te thesecondary-operations such as grinding, cutting or the like.
In another embodiment, the method of producing the gas quenched grade as described above is also particularly useful when used in combination ~vith said coining operation so as to produce precision coining gas quenched particles which substantially eliminate t'ne seco~nu~-~ operations such as grinding, cuttir.g or the lilce. ~n particul~r if h~ b~r found that articles which have a gas quenched composition described herein with relatively small sections do not require molybdenum while heavier parts require the molybdenum.
In particular, it has been found that parts such as clutch backing plates illustrated as 30 in Figure 6, or geo rotors (not shown) may be consistently, accurately manufactured within narrow tolerance variabilities by coining the sintered product.
In particular, the process of precision coining of a sintered article of powder metal consists of the steps of:
1. selecting the elemental iron powder;
2. determining the desired properties of the sintered articles and selecting:
(a) a quantity of carbon, and;
(b) a quantity of ferro m~ng~nese;
to produce an article having a composition of between 0.3~o to 2.5C~c PCr I CA 9 2 / 0 0 5 S S
,.
m~ng~nese, 0.2~o to 0.85% carbon with the remainder being iron and unavoidable impurities;
3 ~inding the ferro all.o~ to a mean particle ~i~e of approYi~m~ate!y 8 to 12 microns and substantially all of the ferro alloy having a particle size of less than 25 microns;
4. introducing a lubricant while blending the carbon and ferro alloy with the elemental iron powder; and 5. pressing the ~ ur~ to form the article;
Conventional means to increase the strength of powder metal articles use up to 8~c nickel, 4% copper and 1.5~o molybdenum, in prealloyed, partially prealloyed, or admixed powders. Furthermore double press double sintering can be used for high performance parts as a means of increasing part density. Conventional elements are expensive and relatively ineffective for generating mechanical properties equivalent to wrought steel products, which comrnonly use the more effective strengthening alloying elements m~ng~nese and chro~
Moreover, conventional technology as disclosed in United States Patent No. 2,402,120 teach pulverizing material such as mill scale to a very fine sized powder, and thereafter reducing the mill scale powder to iron powder without melting it.
Furtherrnore, United States Patent No. 2,289,569 relates generally to powder metallurgy and more particularly to a low melting point alloy powder and to the usage of the low melting point alloy powders in the formation of sintered articles.
Yet another process is disclosed in United States Patent No. 2,027,763 which relates to a process of m~kinE sintered hard metal and consists essentially of steps cormected with the process in the production of hard metal. In particular, United States Patent No. 2,027,763 relates to a process of m~king sintered hard metal which comprisesproducing a spray of dry, finely powdered mixture of fusible metals and a readily fusible ~lxili~ry metal under high pressure producing a spray of adhesive agent customary for binding hard metals under high stress, and so directing the sprays that the spray of metallic powder and the spray of adhesive liquid will meet on their way tn the molds! or within the latter, whereby the mold will become filled with a compact moist mass of metallic powder and finally completing the hard metallic particle thus formed by sintering.
United States Patent No.4,707,332 teaches a process for m~n~lf~cturing structural parts from intermetallic phases capable of sintering by means of special additives which serve at the same time as sintering assists and increase the ductility of the finished structural product.
Moreover, United States Patent No. 4,464,206 relates to a wrought powder metal process for pre-alloyed powder. In particular, United States Patent No. 4,464,206 teaches a process comprising the steps of commllnim~ting substantially non-compactible pre-alloyed metal powders so as to flatten the particles thereof heating the commllninllted particles of metal powder at an elevated temperature, with the particles adhering and forming a mass during heating, crushing the mass of metal powder, compacting the crushed mass of metal powder, sintering the metal powder and hot working the metal powder into a wrought product.
Finally, Goining is a process well known to those persons skilled in the art. However, a comprehensive method of precision coining of powder metal blanks is lacking. For example, United States Patent No. 2,757,446 teaches a method of forming articles from metal powders which includes hot forging the article to a minimum density of 95 % of the theoretical density wherein the entire change of shape of the article takes places in one direction of movement and wherein the minimum internal flow of the particleswithin the article is at least 5 % and finally finishing the forged article.
The processes as described in the prior art above present a relatively less cost effective process to achieve the desired mechanical properties of the sintered product.
An aspect of the invention relates to a coining process for blending, sintering, and coining powder metal articles, that coining process comprising: blending carbon, ferro manganese and lubricant with compressible iron powder to form a blended mixture;pressing said blended mixture to form said articles; sintering said articles in a reducing atmosphere at a temperature of at least 1250C; and coining said sintered articles to a final shape.
~ 1 ~ 4 ~ Q 7 It is another aspect of this invention to provide a process of precision coining a sintered article of powder metal comprising: selecting iron powder; determining the desired properties of said sintered article and selecting; a quantity of carbon; and a quantity of ferro manganese to produce an article having a composition of between 0.3% to 2.0%
manganese, 0.2% to 0.85% carbon with the remainder being iron and unavoidable impurities; grinding separately said ferro manganese to a mean particle size of approximately 8 to 12 microns and substantially all of said ferro manganese having a particle size of less than 25 microns; introducing a lubricant while blending said carbon, and ferro manganese with said iron powder; pressing said mixture to form said article; sintering said article at a temperature between 1,250~C and 1,350~C in a vacuum or reducing atmosphere of 90% blended nitrogen and 10% hydrogen to produce said sintered article of powdered metal; coining said sintered article to a final shape to narrow the dimensional tolerance variability of coined articles and substantially elimin~te secondary operations.
It is a further aspect of the invention to provide a process of gas quenching coined articles of powder metal, that process comprising: blending carbon, ferro m~ng~nese, ferro molybdenum, ferro chromium and lubricant with compressible iron powder;
pressing said blended mixture to form said articles; sintering said articles at a temperature in the range of 1250 C to 1350 C in a reducing atmosphere; coining said articles to a final form; and gas quenching said articles.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0. 3 to 2. 5 % manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 - 4a - 2 ~ ~ 4 6 0 7 ....
microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0. 3 to 2 . 5 % manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0.5 to 2.0% manganese and between 0.2 to 0. 85 % carbon composition where said product is machined or coined to final dimensional requirements.
It is another aspect of the invention to provide an as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having 1.5% manganese and .8% carbon composition where said product is machined or coined to final dimensional requirements.
Description of Drawings These and other features and objections of the invention will now be described in relation to the following drawings:
Figure 1 is a drawing of the prior art mixture of iron alloy.
Figure 2 is a drawing of a mixture of elemental iron, and ferro alloy in accordance with the invention described herein.
2104~7 - s .
Figure 3 is a graph showing the distribution of particle size in accordance with the invention herein.
Figure 4 is representative drawing of a jet mill utilized to produce the particle size of the ferro alloy.
Figure S is a stress strain graph.
Figure 6 illustrates a coin~d part such as a clutch backing plate made in accordance with the invention.
Figure 7 is a dimensional stability graph.
Figure 8 graphically illustrates the narrow variability tolerance of the coined parts.
DESCRIP IION OF THE INVENTION
Sintered Powder Metal Method Figure 1 is a representative view of a rni~cture of powder metal utilized in the prior art which consists of particles of ferro alloy in powder metal technology.
In particular, copper and nickel may be used as the alloying materials, particularly if the powder metal is subjected to conventional temperature of up to 1150 ~ C during the sintering process.
Moreover, other alloying materials such as manganese, chromium, and molybdenum which were alloyed with iron could be added by means of a master alloy although such elements were tied together in the prior art. For example a comrnon master alloyconsists of 22% of m~n~nese, 22~o of chromium and 225~o of molybdenum, with the balance consisting of iron and carbon. The utilization of the elements in a tied form made it difficult to tailor the mechanical properties of the final sintered product for specific applications. Also the cost of the master alloy is very high and uneconomic.
By lltili7.ing ferro alloys which consist of ferro m~nganese, or ferro chromium or ferro molybdenum or ferro vanadium, separately from one another rather than l]tili7in~ a ferro alloy which consists of a combination of iron, with manganese, chromium, molybdenum or vanadium tied together a more accurate control on the desired properties of the finished product may be accomplished so as to produce a methodhaving more flexibility than accomplished by the prior art as well as being more cost effective.
Figure 2 is a representative drawing of the invention to be described herein, which consists of iron particles, Fe having a mixture of ferro alloys 2.
The ferro alloy 2 can be selected from the following groups:
Name Symbol Approx. % of Alloy Element ferro manganese FeMn 78%
ferro chromium FeCr 65%
ferro molybdenum FeMo 71%
ferro vanadium FeVa 75%
ferro silicon FeSi 75%
ferro boron FeB 17.5%
The ferro alloys available in the market place may also contain carbon as well as unavoidable impurities which is well known to those people skilled in the art.
Chromium molybdenum and v~n~(lillm are added to increase the strength of the finished product particularly when the product is subjected to heat treatment after sintering. Moreover, manganese is added to increase the strength of the finished product, particularly if one is not heat treating the product after the sintering stage.
The reason for this is manganese is a powerful ferrite strengthener (up to 4 times more effective than nickel).
Particularly good results are achieved in the method described herein by grinding the ferro alloys so as to have a Dso or mean particle size of 8 to 12 microns and a Dloo of up to 25 microns where subst~nti~lly all particles of the ferro alloys are less than 25 microns as shown in Figure 3. For certain application a finer distribution may be desirable. For example a D50 of 4 to 8 microns and a Dloo of 15 microns.
Many of the processes used in the prior art have previously used a D50 of 15 microns as illustrated by the dotted lines of Figure 3. It has been found that by finely grinding the of the ferro alloy to a fine particle size in an inert atmosphere as described herein a better balance of mechanical properties may be achieved having improved sintered pore morphology. In other words the porosity is smaller and more rounded and more evenly distributed throughout the mass which enhances strength characteristics of the finished product. In particular, powder metal products are produced which are much tougher than have been achieved heretofore.
The ferro alloy powders may be ground by a variety of means so long as the mean particle size is between 8 and 12 microns. For example, the ferro alloy powders may be ground in a ball mill, or an attritor, provided precautions are taken to prevent oxidation of the ground particles and to control the grinding to obtain the desired particle size distribution.
Particularly good results in controlling the particle size as described herein are achieved by utili~ing the jet mill illustrated in Figure 4. In particular, an inert gas such as cyclohexane, nitrogen or argon is introduced into the grinding chamber via nozzles 4 which fluidize and impart high energy to the particles of ferro alloys 6 upward and causes the ferro alloy particles to break up against each other. As the ferro alloy particles grind up against each other and reduce in size they are lifted higher up the chamber by the gas flow and into a classifier wheel 10 which is set at a particular RPM. The particles of ferro alloy enter the classifier wheel 10 where the ferro alloy particles which are too big are returned into the chamber 8 for further grinding while particles which are small enough namely those particles of ferro alloy having a particle size of less than 25 microns pass through the wheel 10 and collect in the collecting zone 12. The grinding of the ferro alloy material is conducted in an inert gas atmosphere as described above in order to prevent oxidization of the ferro alloymaterial. Accordingly, the grinding mill shown in Figure 4 is a totally enclosedsystem. The jet mill which is utilized accurately controls the size of the particles which are ground and produces a distribution of ground particles which are narrowly centralized as shown in Figure 3. The classifier wheel speed is set to obtain a D50 of 8 to 10 microns. The speed will vary with different ferro alloys being ground.
The mechanical properties of a produced powder metal product may be accurately controlled by: .
(a) selecting elemental iron powder;
(b) determining the desired properties of the sintered article and selecting:
(i) a quantity of carbon; and (ii) the ferro alloy(s) from the group of ferro manganese, ferro chromium, ferro molybdenum, and ferro vanadium and selecting the quantity of same;
(c) grinding separately the ferro alloy(s) to a mean particle size of approximately 8 to 12 microns, which grinding may take place in a jet mill as described herein;
(d) introducing a lubricant while blending the carbon and ferro alloy(s) with the elemental iron powder;
(e) pressing the mixture to form the article; and (f~ subjecting the article to a high temperature sintering at a temperature of between 1,250 ~ C and 1,350 ~ C in a reducing atmosphere of, for example 90% nitrogen and 10% hydrogen.
The lubricant is added in a manner well known to those persons skilled in the art so as to assist in the binding of the powder as well as assisting in the ejecting of the product after pressing. The article is formed by pressing the mixture into shape by utilizing the appropriate pressure of, for example, 25 to 50 tonnes per square inch.
The invention disclosed herein utilizes high temperature sintering of 1,250~C to1,350~C and a reducing atmosphere of, for example nitrogen and hydrogen in a 90/10% ratio, or in vacuum. Moreover, the reducing atmosphere in combination with the high sintering temperature reduces or cleans off the surface oxides allowing the particles to form good bonds and the compacted article to develop the appl-opliate strength. A higher temperature is lltili7e~l in order to create the low dew point necessary to reduce the oxides of manganese and chromium which are difficult to reduce. The conventional practice of sintering at 1150~C does not create a sintering regime with the right combination of low enough dew point and high enough temperature to reduce the oxides of chromium, manganese, vanadium and silicon.
Secondary operations such as machining or the like may be introduced after the sintering stage. Moreover, heat treating stages may be introduced after the sintering stage.
Advantages have been realized by utili7ing the invention as described herein. For example, manganese, chromium and molybdenum ferro alloys are utili7e~1 to strengthen the iron which in combination or singly are less expensive than the copper and nickel alloys which have heretofore been used in the prior art. Moreover, manganese appears to be four times more effective in strengthening iron than nickel as 1 % of manganese is approximately equivalent to 4% nickel, and accordingly a cost advantage has been realized.
Furthermore sintered steels with molybdenum, chromium, manganese and vanadium are dimensionally more stable during sintering at high temperatures described herein than are iron-copper-carbon steels (ie. conventional powder metal (P/M) steels).Process control is therefore easier and more cost effective than with conventional P/M
alloys.
Furthermore, the microstructure of the finished product are improved as they exhibit:
(a) well rounded pores;
(b) a homogenous structure;
(c) structure having a much smaller grain size; and (d) a product that is more similar to wrought and cast steels in composition than conventional powder metal steels.
The process described herein allows one to control or tailor the materials which are desired for a particular application.
( 1 ) sinter hardening grades (2) gas quenched grades (3) as sintered grades (4) high strength grades (5) high ductility grades The following chart provides examples of the five grades referred to above as well as the range of compositions that may be lltili7e~l in accordance with the procedure outlined herein.
Alloy Type Composition Typical Mechanical Properties Ultimate Tensile Stren~th Im~act UTS (ksi) ~L/Ib As Sintered Mn: 0.3 - 2.5%90 25 C: 0.2 - 0.85%
~CT l CA 9 2 ~ O 0 5 5 5 21Q~607 Sinter Hardening Mn: 1.0 - 2.0% 120 LS
C: 0.5 - 0.85%
Mo: 0 -1.0%
Gas Quenched Mn: 0.5 - 2.0% 150 15 Mo: 0.5- 1.5%
C: 0 - 0.8%
Cr: 0 -1.0%
High Strength Mn: 0.5 - 2.0% 200 8 Cr: 0.5 - 2.0%
Mo: 0 -1.0%
C: 0.1 - 0.6%
High Ductility Cr: 0.5 - 2.0% 80 15 Mo: 0- 1.0%
C: 0.1 - 0.6%
Particularly good results were achieved with the as sintered grade with 1.5% Mn and Q.Q,C'c_; UTS of 90ksi and imp_cL strength of 2û ft lbs. Otlqer C 01-.~inati5nS e~f 2Iloyirg are possible to produce articles with specifically tailored baIance of properties such as high tollghness and ware resistance.
Moreover good results were achieved with:
(a) sinter hardening grade with 1.5% Mn, 0.5% Mo, and 0.850~G C;
(b) gas quenching grade (i) with 1.5% Mn, 0.5% Mo, and 0.5% C
(ii) with 0.5% Cr, 1.0% Mn, and 0.5% C
(c) high strength grade (i) with 1.0% Mn, 0.5% C, 0.5% Cr, 0.5% Mo (ii) with 1.5% Cr, 0.6~o C, 1.0% Mn, Rollable Grade Moreover, the method described herein may be utilized to produce a sixth grade identified as a rollable grade having the following composition:
PC~ 1 ~A 9, i 0 0 5 5 5 210~6~7 Rollable Grade Cr: O.S - 2.0% 80 15 Mo: 0- 1.0C~o C: 0.1 - 0.6%
Mn: 0 to 0.6~c Coinin~
., It has been found that the method of producing the as sintered grade as described above is particularly useful when used in combination with a coining operation so as to produce precision coining as sintered parts which substantially elimin~te thesecondary-operations such as grinding, cutting or the like.
In another embodiment, the method of producing the gas quenched grade as described above is also particularly useful when used in combination ~vith said coining operation so as to produce precision coining gas quenched particles which substantially eliminate t'ne seco~nu~-~ operations such as grinding, cuttir.g or the lilce. ~n particul~r if h~ b~r found that articles which have a gas quenched composition described herein with relatively small sections do not require molybdenum while heavier parts require the molybdenum.
In particular, it has been found that parts such as clutch backing plates illustrated as 30 in Figure 6, or geo rotors (not shown) may be consistently, accurately manufactured within narrow tolerance variabilities by coining the sintered product.
In particular, the process of precision coining of a sintered article of powder metal consists of the steps of:
1. selecting the elemental iron powder;
2. determining the desired properties of the sintered articles and selecting:
(a) a quantity of carbon, and;
(b) a quantity of ferro m~ng~nese;
to produce an article having a composition of between 0.3~o to 2.5C~c PCr I CA 9 2 / 0 0 5 S S
,.
m~ng~nese, 0.2~o to 0.85% carbon with the remainder being iron and unavoidable impurities;
3 ~inding the ferro all.o~ to a mean particle ~i~e of approYi~m~ate!y 8 to 12 microns and substantially all of the ferro alloy having a particle size of less than 25 microns;
4. introducing a lubricant while blending the carbon and ferro alloy with the elemental iron powder; and 5. pressing the ~ ur~ to form the article;
6. high temperature sintering the article at a temperature between 1,250~C 1,35Q~C in a reducing atmosphere of for example 90% blended nitrogen and 10~ hydrogen so as produce the sintered article of powdered metal; and 7. then coining the sintered article to a final shape so as to narrow the tolerance variability of coined articles and substantially eliminate secondary operations.
Another embodiment of the invention conl~ises:
1. selecting the elemental iron powder;
2. determining the desired properties of the gas quenched grade articles and selecting:
(a) a quantity of carbon, and (b) a quantity of ferro alloys from the group of ferro manganese, ferro molybdenum and ferro chromium so as to produce a sintered blank resulting in a mass having between 0.5 to 2.0% m~n~,~nese, 0.5% to 1.5% molybdenum, between 0 to l.OYo chromium, and between 0 to 0.8% carbon;
3. grinding the ferro alloy to a mean particle size of approximate!y 8 to 12 microns and substantially all of the ferro alloy having a particle size of less than 25 microns;
4. introducing a lubricant while blending the carbon and ferro alloy with the elemental iron powder; and PCT / CA 9 2 ~ 0 0 5 5 5. pressing the rnLl~ture to form the article;
6. high temperature sintering the article at a temperature between 1,250~C 1,350~C in a reducing atmosphere of for example 90~o blended nitrogen and 10% hydrogen so as produce the sintered article of powdered metal; and 7. then coining the sintered article to a final shape so as to narrow the tolerance variability of coined articles and substantially eliminate secondary operations.
In particular, Figure 5 illustrates the stress strain diagram of coining sintered articles having the prior art composition of FeCuC as well as the lower graph which illustrates the stress strain relationship of an article produced in accordance with the method described herein having a composition of between 0.3% to 2.5% manganese, 0.2~ to0.85% carbon, with the remainder being iron and unavoidable impurities. The stress strain diagram of the composition described herein illustrates the plastic zone 32 which allows the sintered blank to move upon coining to its final shape. The as sintered size change variability is less than in conventional PM materials, on coining this variability is further reduced.
More particularly, Figure 7 illustrates two dimensions which have an acceptable tolerance level of between 140.00 to 139.70 as well as a second part having an acceptable tolerance of between 1.51.20 and 1.51.00. The upper portion of the graph in Figure 7 illustrates that a coined article made from a prior art composition of FeCuC (0.1% to 3~o Cu and 0.5% to 0.8% Carbon) has dimensional variability between 139.820 and 139.940 which peaks approximately between said levels. The tolerance variability of the parts produced with a composition of Fe 0.3 to 2.5~ Mn and 0.2 to 0.85~ C is more acceptable since the tolerance variability ranges from 139.840 to 139.880 peaking at 139.860, and since the tolerance variation lies in the middle of the acceptable tolerance range. In other words if the CPK as illustrated in Figure 8 lies in the middle of the acceptable tolerance range a and b, such tolerance variability is desirable particularly since the variation peaks in the middle which takes up approximately one-third of the tolerance.
More particularly, it has been found that the CPK of the coined as sintered article having a composition of Fe 0.3 to 2.5% Mn and 0.2 to 0.85% C has the desirable CPK of greater than or equal to 1.33. If the CPK shifts from this position, it is less desirable. In other words, the CPK illustrated in Figure 7 relating to a composition of Fe 0.3 to 2.5% Mn and 0.2 to 0.85% C is more desirable than the CPK illustrated in the composition of Fe 0.1% to 3% Cu and 0.5% to 0.8% C. (Although the tolerance variability is still acceptable, it does not lie toward the middle range of the acceptable tolerance level).
It has been found that after producing the sintered article by the sintered grade method described above, one can expect a sintered grade of 0.5. However, upon coining of a part made in accordance with the as sintered grade, one can expect to obtain a CPK of greater than or equal to 1.33 which is highly desirable as the coined sintered powder metal parts will be more uniform in dimensional size thus substantially eliminating secondary operations such as grinding or the like.
CP relates to the "Process Capability Index" and is def1ned as CP - Total Tolerance Process Variation The higher the CP the less variation there is in a process. In other words CP
measures the tightness of the spread in the dimensions produced by the process against the acceptable tolerance. The bigger the spread the lower the CP.
The CPK is the combined measure of variation in process and relationship of process average to specification limit (ie. upper and lower limit).
The higher the CPK the more capable a process is to specification. In other words CPK measures the tightness of the spread as ,well as the position of the spread within the acceptable tolerance. A high CPK translates to parts having a narrow tolerance PC~ I CA 9 2 / O ~ 5 ~ ~
spread positioned in the middle of the acceptable tolerance. The CPK can be changed by ch~n~in~ the tooling or process.
Sintered powder metal parts such as clutch backing plates, geo rotors or the like normally require grinding which increases the cost of same and increases the tolerance variability of successively m~n~lf~ctllred parts. By utilizing the process as described herein one is able to tighten down the tolerances of coined as sintered powder metal parts thereby f~çjlitAting the design of more efficient pumps for example due to the tightening of the tolerance levels.
The as sintered powder metal parts produced in accordance with the invention described herein make it possible for sintered material to flow to final dimensional size as the coining takes place in the plastic zone 32 described above.
Aithou~h the preferred e~bodiment as well as the operation and use have ~een specifically described in relation to the drawings, it should be understood thatvariations in the preferred embodiment could be achieved by a person skilled in the trade ~,vithout departing from the spirit of the invention as claimed herein.
Another embodiment of the invention conl~ises:
1. selecting the elemental iron powder;
2. determining the desired properties of the gas quenched grade articles and selecting:
(a) a quantity of carbon, and (b) a quantity of ferro alloys from the group of ferro manganese, ferro molybdenum and ferro chromium so as to produce a sintered blank resulting in a mass having between 0.5 to 2.0% m~n~,~nese, 0.5% to 1.5% molybdenum, between 0 to l.OYo chromium, and between 0 to 0.8% carbon;
3. grinding the ferro alloy to a mean particle size of approximate!y 8 to 12 microns and substantially all of the ferro alloy having a particle size of less than 25 microns;
4. introducing a lubricant while blending the carbon and ferro alloy with the elemental iron powder; and PCT / CA 9 2 ~ 0 0 5 5 5. pressing the rnLl~ture to form the article;
6. high temperature sintering the article at a temperature between 1,250~C 1,350~C in a reducing atmosphere of for example 90~o blended nitrogen and 10% hydrogen so as produce the sintered article of powdered metal; and 7. then coining the sintered article to a final shape so as to narrow the tolerance variability of coined articles and substantially eliminate secondary operations.
In particular, Figure 5 illustrates the stress strain diagram of coining sintered articles having the prior art composition of FeCuC as well as the lower graph which illustrates the stress strain relationship of an article produced in accordance with the method described herein having a composition of between 0.3% to 2.5% manganese, 0.2~ to0.85% carbon, with the remainder being iron and unavoidable impurities. The stress strain diagram of the composition described herein illustrates the plastic zone 32 which allows the sintered blank to move upon coining to its final shape. The as sintered size change variability is less than in conventional PM materials, on coining this variability is further reduced.
More particularly, Figure 7 illustrates two dimensions which have an acceptable tolerance level of between 140.00 to 139.70 as well as a second part having an acceptable tolerance of between 1.51.20 and 1.51.00. The upper portion of the graph in Figure 7 illustrates that a coined article made from a prior art composition of FeCuC (0.1% to 3~o Cu and 0.5% to 0.8% Carbon) has dimensional variability between 139.820 and 139.940 which peaks approximately between said levels. The tolerance variability of the parts produced with a composition of Fe 0.3 to 2.5~ Mn and 0.2 to 0.85~ C is more acceptable since the tolerance variability ranges from 139.840 to 139.880 peaking at 139.860, and since the tolerance variation lies in the middle of the acceptable tolerance range. In other words if the CPK as illustrated in Figure 8 lies in the middle of the acceptable tolerance range a and b, such tolerance variability is desirable particularly since the variation peaks in the middle which takes up approximately one-third of the tolerance.
More particularly, it has been found that the CPK of the coined as sintered article having a composition of Fe 0.3 to 2.5% Mn and 0.2 to 0.85% C has the desirable CPK of greater than or equal to 1.33. If the CPK shifts from this position, it is less desirable. In other words, the CPK illustrated in Figure 7 relating to a composition of Fe 0.3 to 2.5% Mn and 0.2 to 0.85% C is more desirable than the CPK illustrated in the composition of Fe 0.1% to 3% Cu and 0.5% to 0.8% C. (Although the tolerance variability is still acceptable, it does not lie toward the middle range of the acceptable tolerance level).
It has been found that after producing the sintered article by the sintered grade method described above, one can expect a sintered grade of 0.5. However, upon coining of a part made in accordance with the as sintered grade, one can expect to obtain a CPK of greater than or equal to 1.33 which is highly desirable as the coined sintered powder metal parts will be more uniform in dimensional size thus substantially eliminating secondary operations such as grinding or the like.
CP relates to the "Process Capability Index" and is def1ned as CP - Total Tolerance Process Variation The higher the CP the less variation there is in a process. In other words CP
measures the tightness of the spread in the dimensions produced by the process against the acceptable tolerance. The bigger the spread the lower the CP.
The CPK is the combined measure of variation in process and relationship of process average to specification limit (ie. upper and lower limit).
The higher the CPK the more capable a process is to specification. In other words CPK measures the tightness of the spread as ,well as the position of the spread within the acceptable tolerance. A high CPK translates to parts having a narrow tolerance PC~ I CA 9 2 / O ~ 5 ~ ~
spread positioned in the middle of the acceptable tolerance. The CPK can be changed by ch~n~in~ the tooling or process.
Sintered powder metal parts such as clutch backing plates, geo rotors or the like normally require grinding which increases the cost of same and increases the tolerance variability of successively m~n~lf~ctllred parts. By utilizing the process as described herein one is able to tighten down the tolerances of coined as sintered powder metal parts thereby f~çjlitAting the design of more efficient pumps for example due to the tightening of the tolerance levels.
The as sintered powder metal parts produced in accordance with the invention described herein make it possible for sintered material to flow to final dimensional size as the coining takes place in the plastic zone 32 described above.
Aithou~h the preferred e~bodiment as well as the operation and use have ~een specifically described in relation to the drawings, it should be understood thatvariations in the preferred embodiment could be achieved by a person skilled in the trade ~,vithout departing from the spirit of the invention as claimed herein.
Claims (20)
1. A coining process for blending, sintering, and coining powder metal articles, that coining process comprising:
blending carbon, ferro manganese and lubricant with compressible iron powder to form a blended mixture;
pressing said blended mixture to form said articles;
sintering said articles in a reducing atmosphere at a temperature of at least 1250 C; and coining said sintered articles to a final shape;
blending carbon, ferro manganese and lubricant with compressible iron powder to form a blended mixture;
pressing said blended mixture to form said articles;
sintering said articles in a reducing atmosphere at a temperature of at least 1250 C; and coining said sintered articles to a final shape;
2. The coining process of claim 1 wherein said ferro alloy has a mean particle size of approximately 8 to 12 microns and substantially all of said ferro manganese has a particle size of less than 25 microns.
3. The coining process of claim 1 wherein said article has a final composition of between 0.3% to 2.5%, by weight, manganese, between 0.2% to 0.85%, by weight, carbon, with the remainder being iron and unavoidable impurities.
4. The coining process of claim 1 wherein said sintering is undertaken under a vacuum.
5. The coining process of claim 3 wherein said reducing atmosphere is chosen from a) a blended nitrogen-hydrogen atmosphere, or b) a dissociated ammonia atmosphere.
6. The coining process of claim 1 wherein each of said articles has a composition, by weight, of between 0.5 and 2.0 % Manganese, between 0.5 % and 1.5 %
Molybdenum, up to 1.0 % Chromium and up to 0.8 % Carbon.
Molybdenum, up to 1.0 % Chromium and up to 0.8 % Carbon.
7. The coining process of claim 1 wherein said sintering is conducted at a temperature between 1,250°C and 1,350°C.
8. The coining process of claim 7 wherein said ferro alloy is ground in an atmosphere of inert gas and said article has a CPK value greater than 1.33 after coining.
9. A process of precision coining a sintered article of powder metal comprising: (a) selecting iron powder;
(b) determining the desired properties of said sintered article and selecting;
(i) a quantity of carbon; and (ii) a quantity of ferro manganese to produce an article having a composition of between 0.3% to 2.0% manganese, 0.2%
to 0.85% carbon with the remainder being iron and unavoidable impurities;
(c) grinding separately said ferro manganese to a mean particle size of approximately 8 to 12 microns and substantially all of said ferro manganese having a particle size of less than 25 microns;
(d) introducing a lubricant while blending said carbon, and ferro manganese with said iron powder;
(e) pressing said mixture to form said article;
(f) sintering said article at a temperature between 1,250°C and 1,350°C
in a vacuum or reducing atmosphere of 90% blended nitrogen and 10% hydrogen to produce said sintered article of powdered metal;
(g) coining said sintered article to a final shape to narrow the dimensional tolerance variability of coined articles and substantially eliminate secondary operations.
(b) determining the desired properties of said sintered article and selecting;
(i) a quantity of carbon; and (ii) a quantity of ferro manganese to produce an article having a composition of between 0.3% to 2.0% manganese, 0.2%
to 0.85% carbon with the remainder being iron and unavoidable impurities;
(c) grinding separately said ferro manganese to a mean particle size of approximately 8 to 12 microns and substantially all of said ferro manganese having a particle size of less than 25 microns;
(d) introducing a lubricant while blending said carbon, and ferro manganese with said iron powder;
(e) pressing said mixture to form said article;
(f) sintering said article at a temperature between 1,250°C and 1,350°C
in a vacuum or reducing atmosphere of 90% blended nitrogen and 10% hydrogen to produce said sintered article of powdered metal;
(g) coining said sintered article to a final shape to narrow the dimensional tolerance variability of coined articles and substantially eliminate secondary operations.
10. The coining process of claim 1 wherein said coining dimensionally sizes saidcoined sintered article.
11. The process as claimed in claim 9 wherein said tolerance variability has a CPK
of greater than or equal to 1.33.
of greater than or equal to 1.33.
12. The process as claimed in claim 11 wherein said sintered article presents a sintered form deformable to its final shape upon coining.
13. Coined, as sintered articles produced by the process of claim 9 wherein saidarticles have a compacted and sintered mass with composition of between 0.3% to 2.0%
manganese, 0.2% to 0.85% carbon, with the remainder being iron and unavoidable impurities, said articles having a narrow tolerance variability giving a CPK greater than or equal to 1.33.
manganese, 0.2% to 0.85% carbon, with the remainder being iron and unavoidable impurities, said articles having a narrow tolerance variability giving a CPK greater than or equal to 1.33.
14. The articles as claimed in claim 13 wherein said articles comprise at least one clutch backing plate.
15. The articles as claimed in claim 13 wherein said articles comprise a gerotor.
16. A process of gas quenching coined articles of powder metal, that process comprising:
blending carbon, ferro manganese, ferro molybdenum, ferro chromium and lubricant with compressible iron powder;
pressing said blended mixture to form said articles;
sintering said articles at a temperature in the range of 1250 C to 1350 C in a reducing atmosphere;
coining said articles to a final form; and and gas quenching said articles.
blending carbon, ferro manganese, ferro molybdenum, ferro chromium and lubricant with compressible iron powder;
pressing said blended mixture to form said articles;
sintering said articles at a temperature in the range of 1250 C to 1350 C in a reducing atmosphere;
coining said articles to a final form; and and gas quenching said articles.
17. A process as claimed in claim 16 wherein said article has a composition of between 0.5% to 2.0% manganese, between 0.5% to 1.5% molybdenum, 0 to 1.0%
chromium and between 0 to 0.8% carbon.
chromium and between 0 to 0.8% carbon.
18. An as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0.3 to 2.5% manganese and between 0.2 to 0.85% carbon composition where said product is machined or coined to final dimensional requirements.
19. An as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having between 0.5 to 2.0% manganese and between 0.2 to 0.85% carbon composition where said product is machined or coined to final dimensional requirements.
20. An as-sintered ferrous metal product comprising a compacted and sintered mass composed of a blend of iron powder, carbon and ferro manganese alloy having a mean particle size of approximately 8 to 12 microns, subjected to a high temperature sinter so as to result in an as-sintered mass having 1.5% manganese and .8% carbon composition where said product is machined or coined to final dimensional requirements.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA 2104607 CA2104607C (en) | 1992-12-21 | 1992-12-21 | Sintered coining process |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA 2104607 CA2104607C (en) | 1992-12-21 | 1992-12-21 | Sintered coining process |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2104607A1 CA2104607A1 (en) | 1994-06-22 |
| CA2104607C true CA2104607C (en) | 1999-03-09 |
Family
ID=4152193
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA 2104607 Expired - Lifetime CA2104607C (en) | 1992-12-21 | 1992-12-21 | Sintered coining process |
Country Status (1)
| Country | Link |
|---|---|
| CA (1) | CA2104607C (en) |
-
1992
- 1992-12-21 CA CA 2104607 patent/CA2104607C/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| CA2104607A1 (en) | 1994-06-22 |
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Effective date: 20121221 |