CA1103482A - Niobium stabilised sintered products - Google Patents
Niobium stabilised sintered productsInfo
- Publication number
- CA1103482A CA1103482A CA316,883A CA316883A CA1103482A CA 1103482 A CA1103482 A CA 1103482A CA 316883 A CA316883 A CA 316883A CA 1103482 A CA1103482 A CA 1103482A
- Authority
- CA
- Canada
- Prior art keywords
- powder
- niobium
- chromium
- weight
- balance
- 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
- 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
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE:
The invention is concerned with a niobium- or tantalum-stabilised, titanium- and aluminium-free, chromium-bearing, water-atomised metal powder consisting essentially of the following composition by weight: from 0.01 to 0.2% C, from 1.0 to 2% Si, up to 0.5% Mn, from 11 to 30% Cr, up to 25%
Ni, either from 0.05 to 1% Nb or from 0.10 to 2% Ta or a combination of Nb and Ta to give a stoichiometric equivalent to 0.05 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from 0.05 to 0.25% O2, balance Fe and incidental impurities.
Components produced from the metal powder of the invention are stabilized against weld decay and are low in oxide content.
The invention is concerned with a niobium- or tantalum-stabilised, titanium- and aluminium-free, chromium-bearing, water-atomised metal powder consisting essentially of the following composition by weight: from 0.01 to 0.2% C, from 1.0 to 2% Si, up to 0.5% Mn, from 11 to 30% Cr, up to 25%
Ni, either from 0.05 to 1% Nb or from 0.10 to 2% Ta or a combination of Nb and Ta to give a stoichiometric equivalent to 0.05 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from 0.05 to 0.25% O2, balance Fe and incidental impurities.
Components produced from the metal powder of the invention are stabilized against weld decay and are low in oxide content.
Description
3 ~ ~ ~
Thls invention relates to chromium-bearing metal powders, to methods of making such powders and to products ma~ufactured from such powders.
It is known to produce metal powder by water atomisa-; 5 tion techniques. Certain properties of sintered products manufactured from such powders, however, have hitherto not equalled those to be found in similar products produced ~ by the conventional wrought route. This is particularly -; true of stainless and heat resisting steels where oxides, ~ormed during the water atomisation process, adversely effect both the mechanical properties and corrosion resis~
tance of the steels. It is also known that many chromium steel components are subject to 'weld decay' unless the carbon andlor nitrogen present in the steel is stabilized lS by suitable additions to the melt from which the steel is produced of carbide ~ or nitride - forming elements such as aluminium, titanium, tantalum and niobium. 'Weld decay' results from precipitation of chromium carbide andlor ~ chromium nitride in the heat affected zone of the weld.
`~ ~ 20 Depletion of chromium in the matrix surrounding the precipitate results in rapid localised corrosion~
; The presence of certain carbide - and nitride - ~
forming elements such as tLtanlum and aluminium in a melt - produces relat vely high oxide contents in metal products manufactured from powders produced from the melt.
The present invention sets out to provide chromium-bearing water atomised powders stabilized against weld ." ' .
''' ,'' ' .
.: .
:,' :
decay from which rnetal products low in oxide content can be produced~ Such powders include both chromium-steel and chromium-bearing alloy powders According to the invention, there is pro~ided a niobium- or tantalum-stabilised, titanium- and aluminium-free, - chromium-bearing, water-atomised metal powder consisting essen-tially of the following composition by weight: from 0.01 to 0.2%
C, from l.0 to 2% Si, up to 0.5% Mn, from ll to 30% Cr, up to : 25% Ni, either from 0.05 to 1% Nb or from 0.10 to 2% Ta or a combination of Nb and Ta to give a stoichiometric equivalent - to 0.05 to 1% Nb, up to 5% Mo, up to 1% V/ up to 2% Cu, and from 0.05 to 0.25% 2~ balance Fe and incidental impurities.
- A preferred ferritic steel powder in accordance with ~` the present invention consists of a coMposition falling within the followlng ranges, by weight: from 0.01 to 0.2~C, 2rom 1 to 2~ Si, up to .5~, from llto 30%Cr, up to 5% Ni, from ~ 0.10 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from : : 0.1 to 0.2~ 2' balance Fe and incidental impurities.
, .:
- A preferred austenetic skeel powder in accordance :: 20 with the present invention consists of a composition falling ; within the following ranges, by weight: from 0.01 to 0.2% C, from l to 2~ Si, up to.5% Mn, from ll to 30% Cr, from 5 to . 256 Ni, from 0.10 to 1% Nb, up to 5% Mo, up to 1% V, up to 2%
Cu, and from 0.1 to 0.2% 2' balance Fe and incidental impurities.
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~ ~39~2 From Table 1 it will be seen that the two titanium-stabilized powders J and K have relatively high oxygen contents:
,~ 0.54 wt% and 0.46 wt% respectively.~ This is because during the water atomisation process, titanium oxidises to form titanium oxide; which is irreducable. Thus the use of titanium to stabilise carbon to avoid,weld decay leads to high residual , oxide contents in the powder and in any article produced from the powder.
, Likewise an aluminium-stabilized powder would have , 10 a relatively high oxygen content for the same reason as given ,~ ~ above for titanium-stabiliæed powder. Thus, the use of aluminium .~
to stabilise nitrogen to avoid weld decay would also lead to ; high residual oxide contents in the powder and in any article produced from the powder.
The niobium-stabilized powders A to I, however, all ' ' have relatively low oxygen contents of less than 0.2 wt% and, '", with the exception of powder A, contain 0.15~ by weight or less.
The oxygen content of powder C will be seen to be similar to . that o~ a niobium-free equivalent (powder L) indicating that the addition of niobium to the melt has no significant effect , ,~ upon the oxygen content of the powder; simi-larly, tantalum.
, When compacts of unstabilized water atomised powder are sintered, a reac,tion occurs between the carbon and oxygen present in the powder to form carbon monoxide. This reaction has the important effect of reducing the oxygen content of the product to provide good mechanical properties and . .
., ';;
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corrosion resistance and to permit the production of products having relatively low carbon contents.
Only carbide - and nitride - forming elements which do not suppress this reducing reaction can, consequently be 5 used to produce stabilized sintered.steel products low in oxygen and carbon (i.e. oxygen and carbon contents : respectively less than 0.05% by wt.) having mechanical and corrosion resistant prsperties equivalent to those to be found in wrought products~ :
Table 2 below shows the change in carbon and oxygen ~ , . levels observed during sintering of two niobium-stabiIized ~: powders.
Table 2 Reduction of Oxygen & Carbon During Sintering .,,' ~ ~
REFE~ENCE POWDER COMPOSITION SINTERED PRODUCT COMPO.SITION
. C 2 C 2 .
G ~ 0.033 0.14 0,003 0.10 H 0.18 ~.14 0.088 0.04 ~-- ~ 20 Powder H was compacted in a dle to produce a compact .` ~ which was slntered in an atmosphere comprising 80% argon/
20% hydrogen at a temperature of 1350C for a period of~
3 minutes. During sintering, the oxygen content reduced from 0~14 to 0.04 weight % and the carbon content from 0.18 ; 25 to 0.033 wt%.
:~ Powder G was fed to the nip of a pair of compaction rolls to produce a green strip which was sintered in an .
~ e ; .
. .
atmosphere comprising 80% argon/20% hydrogen at a tempera-ture of 1350C for 3 minutes. During sintering, the oxygen content of the green strip reduced from 0.14 to 0.10 wt%
and the carbon content from O033 to .003 wt%.
From these two trlals, it can be concluded that :
; niobi~ does not suppress the carbon/oxygen reaction during sintering.
Strip produced from Powder L (that is to say an UTI-stabilized stainless steel) was found to be subject to weld decay. Samples of welded strip produced from this . ~ ~ .
powder failed rapidly when immersed in a 3% sodium chloride -- solution. By contrast, strip produced from Powder C
niobium-stabilized stainless powder) was found to be immune to weld decay. Thus niobium was shown to be effe~tive in st~bilizing the carbon present in the strip.
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Thls invention relates to chromium-bearing metal powders, to methods of making such powders and to products ma~ufactured from such powders.
It is known to produce metal powder by water atomisa-; 5 tion techniques. Certain properties of sintered products manufactured from such powders, however, have hitherto not equalled those to be found in similar products produced ~ by the conventional wrought route. This is particularly -; true of stainless and heat resisting steels where oxides, ~ormed during the water atomisation process, adversely effect both the mechanical properties and corrosion resis~
tance of the steels. It is also known that many chromium steel components are subject to 'weld decay' unless the carbon andlor nitrogen present in the steel is stabilized lS by suitable additions to the melt from which the steel is produced of carbide ~ or nitride - forming elements such as aluminium, titanium, tantalum and niobium. 'Weld decay' results from precipitation of chromium carbide andlor ~ chromium nitride in the heat affected zone of the weld.
`~ ~ 20 Depletion of chromium in the matrix surrounding the precipitate results in rapid localised corrosion~
; The presence of certain carbide - and nitride - ~
forming elements such as tLtanlum and aluminium in a melt - produces relat vely high oxide contents in metal products manufactured from powders produced from the melt.
The present invention sets out to provide chromium-bearing water atomised powders stabilized against weld ." ' .
''' ,'' ' .
.: .
:,' :
decay from which rnetal products low in oxide content can be produced~ Such powders include both chromium-steel and chromium-bearing alloy powders According to the invention, there is pro~ided a niobium- or tantalum-stabilised, titanium- and aluminium-free, - chromium-bearing, water-atomised metal powder consisting essen-tially of the following composition by weight: from 0.01 to 0.2%
C, from l.0 to 2% Si, up to 0.5% Mn, from ll to 30% Cr, up to : 25% Ni, either from 0.05 to 1% Nb or from 0.10 to 2% Ta or a combination of Nb and Ta to give a stoichiometric equivalent - to 0.05 to 1% Nb, up to 5% Mo, up to 1% V/ up to 2% Cu, and from 0.05 to 0.25% 2~ balance Fe and incidental impurities.
- A preferred ferritic steel powder in accordance with ~` the present invention consists of a coMposition falling within the followlng ranges, by weight: from 0.01 to 0.2~C, 2rom 1 to 2~ Si, up to .5~, from llto 30%Cr, up to 5% Ni, from ~ 0.10 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from : : 0.1 to 0.2~ 2' balance Fe and incidental impurities.
, .:
- A preferred austenetic skeel powder in accordance :: 20 with the present invention consists of a composition falling ; within the following ranges, by weight: from 0.01 to 0.2% C, from l to 2~ Si, up to.5% Mn, from ll to 30% Cr, from 5 to . 256 Ni, from 0.10 to 1% Nb, up to 5% Mo, up to 1% V, up to 2%
Cu, and from 0.1 to 0.2% 2' balance Fe and incidental impurities.
`~ , :`
`"`~i~
~1~3~2 .','', ' a~ u~ Q) Q~ U~ ~ :'~
.0 u ~ ~ a ~ a a a a ~ al ~ ~ r~ u ¦ ~ R , I Z ~ ~ ~ ~ ~; z ... ~. . . . 00 ~
. ~ ~
In N O O O ~ O O C O O
O O
'` . . .
.',' ~'. O~ t`;l ~ ' ~1 t~ t`l ~1 1~') Ll", l ,~, O O 0 O O O O O 0:, ~
~;~ U ¦ o ¦ ~ O I l I l I l I l I r` 1 ' 1 ~; ~1r~ o~ ~1 O O t~
O ~ _J ~ ~1 ,~ o o o o o ô o o o o o too n N ~ r~ 1~ ~:
,'~ ''~0 ' O ,1 ,1 rO) O O O uO) O) O ~
1 1 I 1 1 1 1 1 1 l ~; 1~ 1~ 1 la IW 1~ IH I
, ~n u~
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~n t, a)~ .
U~ .,, ~ ,, V
æ ~ , Q ~
:~ u~ ~ a) ~ ~ o - ~ .~ ~ ~ h O
E~ .
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~`'` '. .
' ~ ',, ~ 0~ ~P U~ . .
~' : O 0 ' ' ~'' , ' ' ~ . :
e ~
.. "~ '~ ~r l :: :: .
;~ O . ~
U~ ~ . ~
W 1 ~
'~" . ~r ' ' :::
- ~ O O . -' , :' .' .~' 'U~ In ~
i. . . ' .... ~. ~ O . .
.: . . . ., . .. .... ~ ~
~ ~39~2 From Table 1 it will be seen that the two titanium-stabilized powders J and K have relatively high oxygen contents:
,~ 0.54 wt% and 0.46 wt% respectively.~ This is because during the water atomisation process, titanium oxidises to form titanium oxide; which is irreducable. Thus the use of titanium to stabilise carbon to avoid,weld decay leads to high residual , oxide contents in the powder and in any article produced from the powder.
, Likewise an aluminium-stabilized powder would have , 10 a relatively high oxygen content for the same reason as given ,~ ~ above for titanium-stabiliæed powder. Thus, the use of aluminium .~
to stabilise nitrogen to avoid weld decay would also lead to ; high residual oxide contents in the powder and in any article produced from the powder.
The niobium-stabilized powders A to I, however, all ' ' have relatively low oxygen contents of less than 0.2 wt% and, '", with the exception of powder A, contain 0.15~ by weight or less.
The oxygen content of powder C will be seen to be similar to . that o~ a niobium-free equivalent (powder L) indicating that the addition of niobium to the melt has no significant effect , ,~ upon the oxygen content of the powder; simi-larly, tantalum.
, When compacts of unstabilized water atomised powder are sintered, a reac,tion occurs between the carbon and oxygen present in the powder to form carbon monoxide. This reaction has the important effect of reducing the oxygen content of the product to provide good mechanical properties and . .
., ';;
' . I .
: .
' ' .
- - \
~:~CE3qL8~
corrosion resistance and to permit the production of products having relatively low carbon contents.
Only carbide - and nitride - forming elements which do not suppress this reducing reaction can, consequently be 5 used to produce stabilized sintered.steel products low in oxygen and carbon (i.e. oxygen and carbon contents : respectively less than 0.05% by wt.) having mechanical and corrosion resistant prsperties equivalent to those to be found in wrought products~ :
Table 2 below shows the change in carbon and oxygen ~ , . levels observed during sintering of two niobium-stabiIized ~: powders.
Table 2 Reduction of Oxygen & Carbon During Sintering .,,' ~ ~
REFE~ENCE POWDER COMPOSITION SINTERED PRODUCT COMPO.SITION
. C 2 C 2 .
G ~ 0.033 0.14 0,003 0.10 H 0.18 ~.14 0.088 0.04 ~-- ~ 20 Powder H was compacted in a dle to produce a compact .` ~ which was slntered in an atmosphere comprising 80% argon/
20% hydrogen at a temperature of 1350C for a period of~
3 minutes. During sintering, the oxygen content reduced from 0~14 to 0.04 weight % and the carbon content from 0.18 ; 25 to 0.033 wt%.
:~ Powder G was fed to the nip of a pair of compaction rolls to produce a green strip which was sintered in an .
~ e ; .
. .
atmosphere comprising 80% argon/20% hydrogen at a tempera-ture of 1350C for 3 minutes. During sintering, the oxygen content of the green strip reduced from 0.14 to 0.10 wt%
and the carbon content from O033 to .003 wt%.
From these two trlals, it can be concluded that :
; niobi~ does not suppress the carbon/oxygen reaction during sintering.
Strip produced from Powder L (that is to say an UTI-stabilized stainless steel) was found to be subject to weld decay. Samples of welded strip produced from this . ~ ~ .
powder failed rapidly when immersed in a 3% sodium chloride -- solution. By contrast, strip produced from Powder C
niobium-stabilized stainless powder) was found to be immune to weld decay. Thus niobium was shown to be effe~tive in st~bilizing the carbon present in the strip.
.'',','- . '~ .
., :
_ . .. _ . . . . .
. , .
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... .
.; ,~ .
., .
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,
Claims (5)
1. A niobium- or tantalum-stabilised, titanium-and aluminium-free, chromium-bearing, water-atomised metal powder consisting essentially of the following composition by weight: from 0.01 to 0.2% C, from 1.0 to 2% Si, up to 0.5% Mn, from 11 to 30% Cr, up to 25% Ni, either from 0.05 to 1% Nb or from 0.10 to 2% Ta or a combination of Nb and Ta to give a stoichiometric equivalent to 0.05 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from 0.05 to 0.25% O2, balance Fe and incidental impurities.
2. A powder, as claimed in claim 1, consisting essentially of the following composition by weight: from 0.01 to 0.2% C, from 1 to 2% Si, up to .5% Mn, from 11 to 30% Cr, up to 5% Ni, from 0.10 to 1% Nb, up to 5% Mo, up to 1% V, up to 2% Cu, and from 0.1 to 0.2% O2, balance Fe and incidental impurities.
3. A powder, as claimed in claim 1, consisting essentially of the following composition by weight: from 0.01 to 0.2% C, from 1 to 2% Si, up to .5% Mn, from 11 to 30% Cr, from 5 to 25% Ni, from 0.10 to 1% Nb, up to 5% Mo, up to 1% V/ up to 2% Cu, and from 0.1 to 0.2% O2, balance Fe and incidental impurities.
4. A method of making metal products by compacting a niobium- or tantalum-stabilised, titanium- and aluminium-free, chromium-bearing, water-atomised metal powder having the composition claimed in any one of claims 1 to 3 to produce a compact and subsequently sintering the compact in a reducing atmosphere.
5. A metal product produced by compacting and sintering a metal powder as defined in any one of claims 1 to 3.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB49627/77 | 1977-11-29 | ||
| GB4962777 | 1977-11-29 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1103482A true CA1103482A (en) | 1981-06-23 |
Family
ID=10453001
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA316,883A Expired CA1103482A (en) | 1977-11-29 | 1978-11-27 | Niobium stabilised sintered products |
Country Status (9)
| Country | Link |
|---|---|
| JP (1) | JPS5499718A (en) |
| BE (1) | BE872317A (en) |
| CA (1) | CA1103482A (en) |
| DE (1) | DE2851274A1 (en) |
| FR (1) | FR2410053B1 (en) |
| GB (1) | GB2009236B (en) |
| IT (1) | IT1160977B (en) |
| LU (1) | LU80588A1 (en) |
| SE (1) | SE7812236L (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2669937B1 (en) * | 1990-12-04 | 1993-11-12 | Tecphy | STAINLESS STEEL FOR USE IN PARTICULAR FOR THE PRODUCTION OF COATING OF HOT WORKING TOOLS AND TOOLS COMPRISING A COATING IN SUCH A STAINLESS STEEL. |
| US20030077200A1 (en) * | 2000-07-07 | 2003-04-24 | Craig Charles H. | Enhanced radiopaque alloy stent |
| JP6299612B2 (en) * | 2015-01-08 | 2018-03-28 | セイコーエプソン株式会社 | Metal powder for powder metallurgy, compound, granulated powder and sintered body |
| DK3333275T3 (en) * | 2016-12-07 | 2021-02-08 | Hoeganaes Ab Publ | STAINLESS STEEL POWDER FOR THE MANUFACTURE OF STAINLESS DUPLEX SINTER STEEL |
| US11970760B2 (en) * | 2021-11-10 | 2024-04-30 | Daido Steel Co., Ltd. | Metal powder |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1089792B (en) * | 1957-02-08 | 1960-09-29 | Deutsche Edelstahlwerke Ag | Use of a steel for sintered, porous, corrosion-resistant bodies and processes for their production |
| DE1558654A1 (en) * | 1967-12-21 | 1970-07-23 | Schwaebische Huettenwerke Gmbh | Sintered iron alloy and process for its manufacture |
| US3451809A (en) * | 1968-03-08 | 1969-06-24 | Int Nickel Co | Method of sintering maraging steel with boron additions |
| DE2003611A1 (en) * | 1970-01-28 | 1971-08-12 | Schwaebische Huettenwerke Gmbh | Sintered iron-tantalum alloy prod |
-
1978
- 1978-11-27 DE DE19782851274 patent/DE2851274A1/en not_active Withdrawn
- 1978-11-27 BE BE191969A patent/BE872317A/en not_active IP Right Cessation
- 1978-11-27 CA CA316,883A patent/CA1103482A/en not_active Expired
- 1978-11-28 LU LU80588A patent/LU80588A1/en unknown
- 1978-11-28 GB GB7846325A patent/GB2009236B/en not_active Expired
- 1978-11-28 JP JP14705978A patent/JPS5499718A/en active Pending
- 1978-11-28 SE SE7812236A patent/SE7812236L/en unknown
- 1978-11-29 IT IT69732/78A patent/IT1160977B/en active
- 1978-11-29 FR FR7833664A patent/FR2410053B1/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| BE872317A (en) | 1979-03-16 |
| JPS5499718A (en) | 1979-08-06 |
| FR2410053B1 (en) | 1985-10-18 |
| SE7812236L (en) | 1979-05-30 |
| GB2009236A (en) | 1979-06-13 |
| DE2851274A1 (en) | 1979-05-31 |
| FR2410053A1 (en) | 1979-06-22 |
| IT1160977B (en) | 1987-03-11 |
| LU80588A1 (en) | 1979-03-22 |
| IT7869732A0 (en) | 1978-11-29 |
| GB2009236B (en) | 1982-02-17 |
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| MKEX | Expiry |