EP3333275B1 - Stainless steel powder for producing sintered duplex stainless steel - Google Patents
Stainless steel powder for producing sintered duplex stainless steel Download PDFInfo
- Publication number
- EP3333275B1 EP3333275B1 EP16202574.6A EP16202574A EP3333275B1 EP 3333275 B1 EP3333275 B1 EP 3333275B1 EP 16202574 A EP16202574 A EP 16202574A EP 3333275 B1 EP3333275 B1 EP 3333275B1
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- EP
- European Patent Office
- Prior art keywords
- stainless steel
- microns
- powder
- steel powder
- prealloyed
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- 239000000843 powder Substances 0.000 title claims description 120
- 229910001220 stainless steel Inorganic materials 0.000 title claims description 77
- 239000010935 stainless steel Substances 0.000 title claims description 42
- 229910001039 duplex stainless steel Inorganic materials 0.000 title claims description 25
- 239000002245 particle Substances 0.000 claims description 34
- 239000000203 mixture Substances 0.000 claims description 27
- 229910052757 nitrogen Inorganic materials 0.000 claims description 23
- 238000001816 cooling Methods 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 22
- 238000000034 method Methods 0.000 claims description 21
- 238000005245 sintering Methods 0.000 claims description 21
- 239000012535 impurity Substances 0.000 claims description 12
- 238000005056 compaction Methods 0.000 claims description 11
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- 229910052735 hafnium Inorganic materials 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 9
- 239000000654 additive Substances 0.000 claims description 8
- 229910052796 boron Inorganic materials 0.000 claims description 8
- 238000007596 consolidation process Methods 0.000 claims description 8
- 230000000996 additive effect Effects 0.000 claims description 5
- 238000009689 gas atomisation Methods 0.000 claims description 5
- 239000000314 lubricant Substances 0.000 claims description 5
- 238000009692 water atomization Methods 0.000 claims description 5
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 4
- 239000011230 binding agent Substances 0.000 claims description 3
- 238000001513 hot isostatic pressing Methods 0.000 claims description 3
- 238000001746 injection moulding Methods 0.000 claims description 3
- 238000002156 mixing Methods 0.000 claims description 3
- 239000012071 phase Substances 0.000 description 47
- 230000007797 corrosion Effects 0.000 description 38
- 238000005260 corrosion Methods 0.000 description 38
- 239000011651 chromium Substances 0.000 description 28
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 21
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 20
- 229910001566 austenite Inorganic materials 0.000 description 20
- 238000004663 powder metallurgy Methods 0.000 description 17
- 239000010949 copper Substances 0.000 description 16
- 229910000859 α-Fe Inorganic materials 0.000 description 16
- 229910000831 Steel Inorganic materials 0.000 description 15
- 229910045601 alloy Inorganic materials 0.000 description 15
- 239000000956 alloy Substances 0.000 description 15
- 239000010959 steel Substances 0.000 description 15
- 229910052804 chromium Inorganic materials 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 11
- 239000011572 manganese Substances 0.000 description 11
- 229910052750 molybdenum Inorganic materials 0.000 description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 230000002939 deleterious effect Effects 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 9
- 239000010955 niobium Substances 0.000 description 9
- 229910052721 tungsten Inorganic materials 0.000 description 9
- TVZRAEYQIKYCPH-UHFFFAOYSA-N 3-(trimethylsilyl)propane-1-sulfonic acid Chemical compound C[Si](C)(C)CCCS(O)(=O)=O TVZRAEYQIKYCPH-UHFFFAOYSA-N 0.000 description 8
- 229910052759 nickel Inorganic materials 0.000 description 8
- 239000000126 substance Substances 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 229910052802 copper Inorganic materials 0.000 description 7
- 239000007789 gas Substances 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 229910052710 silicon Inorganic materials 0.000 description 7
- 238000003466 welding Methods 0.000 description 7
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- 229910052739 hydrogen Inorganic materials 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 5
- 150000004767 nitrides Chemical class 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 4
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000000137 annealing Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 239000003381 stabilizer Substances 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- -1 e.g. Substances 0.000 description 3
- 238000001125 extrusion Methods 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000001465 metallisation Methods 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- 229910021529 ammonia Inorganic materials 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 238000000149 argon plasma sintering Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 230000001788 irregular Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000012805 post-processing Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- UGFAIRIUMAVXCW-UHFFFAOYSA-N Carbon monoxide Chemical compound [O+]#[C-] UGFAIRIUMAVXCW-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910000593 SAF 2205 Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 229910000278 bentonite Inorganic materials 0.000 description 1
- 239000000440 bentonite Substances 0.000 description 1
- SVPXDRXYRYOSEX-UHFFFAOYSA-N bentoquatam Chemical compound O.O=[Si]=O.O=[Al]O[Al]=O SVPXDRXYRYOSEX-UHFFFAOYSA-N 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 229910001634 calcium fluoride Inorganic materials 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 238000001311 chemical methods and process Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009770 conventional sintering Methods 0.000 description 1
- 239000000112 cooling gas Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010612 desalination reaction Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- YGANSGVIUGARFR-UHFFFAOYSA-N dipotassium dioxosilane oxo(oxoalumanyloxy)alumane oxygen(2-) Chemical compound [O--].[K+].[K+].O=[Si]=O.O=[Al]O[Al]=O YGANSGVIUGARFR-UHFFFAOYSA-N 0.000 description 1
- 238000002848 electrochemical method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- HGPXWXLYXNVULB-UHFFFAOYSA-M lithium stearate Chemical compound [Li+].CCCCCCCCCCCCCCCCCC([O-])=O HGPXWXLYXNVULB-UHFFFAOYSA-M 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 238000003913 materials processing Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 238000009740 moulding (composite fabrication) Methods 0.000 description 1
- 229910052627 muscovite Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000011236 particulate material Substances 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 230000003449 preventive effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007873 sieving Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 229910052714 tellurium Inorganic materials 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000000080 wetting agent Substances 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
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- 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
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- 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%
- C22C33/0271—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5% with only C, Mn, Si, P, S, As as alloying elements, e.g. carbon steel
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- 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%
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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- B22—CASTING; POWDER METALLURGY
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
- B22F2009/0828—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid with water
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/05—Light metals
- B22F2301/058—Magnesium
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- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/10—Copper
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- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/15—Nickel or cobalt
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2304/00—Physical aspects of the powder
- B22F2304/10—Micron size particles, i.e. above 1 micrometer up to 500 micrometer
Definitions
- Embodiments of the present invention may provide a new stainless steel powder suitable for manufacturing of sintered duplex stainless steels. Embodiments of the present invention may also relate to a method for producing the sintered duplex stainless steel.
- Duplex stainless steels have been known to the industry for more than 60 years. They are widely used in heat-treated cast, wrought and gas atomized powder forms, in many applications that require a combination of high strength and high corrosion resistance. However, they are unavailable today, in the water atomized powder form for use in press and sinter applications.
- duplex stainless steels Common uses for duplex stainless steels include chemical process plants pipeline, petrochemical industry, power plants and automobiles. They are also used in food processing industry, pharmaceutical process components, paper and pulp industry, in desalination plants and in the mining industry. Duplex stainless steels are known for their high resistance to inter granular corrosion (IGC) and stress corrosion cracking (SCC) in chloride media. Chloride is severe challenge that leads to rapid corrosion media for iron-based alloys.
- ITC inter granular corrosion
- SCC stress corrosion cracking
- austenite stabilizers e.g., nickel (Ni), manganese (Mn), carbon (C), nitrogen (N), copper (Cu) and cobalt (Co)
- ferrite stabilizers e.g., chromium (Cr), silicon (Si), molybdenum (Mo), tungsten (W), titanium (Ti) and niobium (Nb).
- duplex stainless steel As mentioned previously, the high strength and high corrosion resistance of duplex stainless steel is believed to come from a balance of ferrite and austenite in the microstructure.
- the microstructure depends not only on the chemistry but also on the heat treatment carried out on the material.
- All duplex steel compositions today make use of N in the chemistry, as N is a strong austenite stabilizer. N, when present in the alloy along with Cr, poses problem of forming nitrides which are deleterious to the properties such as strength and corrosion resistance.
- an intermetallic phase known as "Sigma” is formed in a heat affected zone (HAZ) due to slower cooling rates.
- HZ heat affected zone
- This Sigma phase is a hard, supersaturated, intermetallic phase containing Cr and Mo. The area around the Sigma phase is depleted of Cr and Mo and becomes weak and less resistant to corrosion. Often duplex stainless steels need annealing and quenching process to reduce or eliminate this Sigma phase.
- the steel In wrought or cast duplex stainless steels, the steel is solidified as ferritic steel and the austenite phase is precipitated out from ferrite during cooling of the alloy.
- the cooling rate is critical after casting or any heat treatment, as the cooling rate determines the percentage of austenite and any intermetallic phases precipitated within the structure.
- Typical composition of wrought duplex stainless steel is Fe with 32-23wt% Cr, 4.5-6.5wt% Ni, 2.5-3.5wt% Mo, and 0.08-0.2wt% N, such as for SAF 2205.
- the main obstacle in using low cost water atomized powders for conventional PM use is increased N and possibility of intermetallic and carbide precipitation due to cooling rate during the sintering.
- conventional sintering needs some wetting agents or low temperature melting constituents to increase free energy and accelerate the kinetics of austenite phase precipitation within ferritic matrix.
- SE538577C2 discloses a sintered duplex stainless steel made from gas atomized powder and having a chemical composition with a max 0.030wt% C, 4.5-6.5wt% Ni, 0.21-0.29wt% N, 3.0-3.5wt% Mo, 21-24wt% Cr, and optionally one or more of 0-1.0wt% Cu, 0-1.0wt% W, 0-2.0wt% Mn, 0-1.0wt% Si wherein N is equal or greater than 0.01*Cr and the remaining elements are Fe and unavoidable impurities.
- EP0167822A1 discloses a sintered stainless steel comprising a matrix phase and a dispersed phase and a process for manufacturing.
- the dispersed phase is an austenite metallurgical structure and is dispersed throughout the matrix phase, which is comprised of an austenitic metallurgical structure having a steel composition different from that of the dispersed phase or a ferritic-austenitic duplex stainless steel.
- JP5263199A discloses production of a sintered stainless steel comprising a matrix phase and a dispersing phase.
- the method includes mixing a ferritic stainless steel powder with a powder selected from an austenitic stainless steel powder, an austenitic-ferritic duplex stainless steel powder, an austenitic-martensitic duplex stainless steel powder and austenitic-ferritic-martensitic stainless triple phase stainless steel powder.
- the powder mixture being compacted and sintered.
- EP0534864B1 (Sumitomo) discloses a sintered stainless steel having a content of N of 0.10-0.35wt% and made from gas atomized steel powder having the same chemical composition as the sintered stainless steel.
- N content helps the above properties, it can pose hurdles in post processing, such as heat treatment and welding operations, by forming chromium nitrides, which limits the use of duplex stainless steels in many applications.
- powder form N increases the powder hardness making it less suitable for press and sinter applications.
- Embodiments of the invention overcome the problem with nitrides by avoiding the use of N in the chemistry, for example, having less than 0.10 wt% N or less than 0.07 wt% N, or less than 0.06 wt% N, or less than 0.05 wt% N, or less 0.04 wt% N, or less than 0.03 wt% N, and achieving phase balance and strength by alternative elements.
- Embodiments of the invention may enable production of water atomized powder with moderate compressibility for use in conventional press and sinter applications.
- Embodiments of this composition may also reduce precipitation of a deleterious 'Sigma' phase; irrespective of rate of cooling during sintering or annealing, mainly due to lower Mo content. Thus minimizing post sintering heat treatments necessary to eliminate "Sigma" phase and minimizing Sigma phase precipitation during welding.
- Embodiments of the composition may offer similar advantages when formed by gas atomization.
- compositions yield similar properties when processed with Casting, Direct Metal Deposition and Additive Manufacturing techniques.
- One object of certain embodiments of the invention is to provide an alloy powder for conventional PM that will produce a duplex structure during a sintering cycle.
- Another object of certain embodiments of the present invention is to obtain at least 35% higher tensile strength than ferritic steels such as 430L and double the corrosion resistance than austenitic steels such as 316L.
- Still another object of certain embodiments of the present invention is to provide a method for producing a duplex sintered stainless steel without the need of post sintering heat treatment.
- a stainless steel powder comprising, or consisting of, in weight percent:
- the unavoidable impurities do not include the listed elements of C, Si, Mn, Cr, Ni, Mo, W, N, Cu, P, S, B, Nb, Hf, Ti, or Co.
- Unavoidabale impurties may include impurities that cannot be controlled, or controlled with difficulty, during manufacture of steels. These can come from the raw materials used and also from the process. These include, Al, O, Mg, Ca, Ta, V, Te, or Sn.
- the unavoidable impurities may be up to 0.8wt%, up to 0.6wt%, up to 0.3wt%.
- An unavoidable impurity may be O. O may be present up to 0.6wt%, up to 0.4wt%, or up to 0.3wt%.
- a stainless steel powder consisting of, in weight percent:
- the powder is ferritic.
- ferritic For example, 99.5% ferritic. Slight amounts of austenite, e.g., up to 0.5% may be tolerated.
- the powder is produced by water atomization.
- the powder is produced by gas atomization.
- the particle size of the powder is between 53 microns and 18 microns such that at least 80wt% of the particles are less than 53 microns and at most 20wt% of the particles are less than 18 microns.
- the particle size of the powder is between 26 microns and 5 microns such that at least 80wt% of the particles are less than 26 microns and at most 20wt% of the particles are less than 5 microns.
- the particle size of the powder is between 150 microns and 26 microns such that at least 80wt% of the particles are less than 150 microns and at most 20wt% of the particles are less than 26 microns.
- Examples of an inert atmosphere include nitrogen, argon, and vacuum with argon backfill.
- An example of a reducing atmosphere is a hydrogen atmosphere, an atmosphere of a mixture of hydrogen and nitrogen, or an atmosphere of dissociated ammonia.
- a hydrogen atmosphere an atmosphere of a mixture of hydrogen and nitrogen, or an atmosphere of dissociated ammonia.
- carbon dioxide or carbon monoxide atmospheres may be used.
- said consolidation process includes one of: Metal Injection Molding (MIM), Hot Isostatic Pressing (HIP) or Additive Manufacturing techniques such as Binder Jetting, Laser Powder Bed Fusion (L-PBF), Direct Metal Laser Sintering (DMLS) or Direct Metal Deposition (DMD).
- MIM Metal Injection Molding
- HIP Hot Isostatic Pressing
- Additive Manufacturing techniques such as Binder Jetting, Laser Powder Bed Fusion (L-PBF), Direct Metal Laser Sintering (DMLS) or Direct Metal Deposition (DMD).
- forced cooling or quenching is excluded from the cooling step.
- Cr is a major element in stainless steels which forms a Cr 2 O 3 layer on the surface which then prevents further oxygen passing the layer, therefore providing an increased corrosion resistance.
- Ni is another major element which affects the properties of stainless steel. Ni increases the strength and toughness of the steel and also when present with Cr, enhances the corrosion resistance. Mo and W both impart the strength and toughness when present along with Ni. Mo also enhances the corrosion resistance along with Cr and Ni. Si acts as deoxidizer preventing O combining in the steel during melting and also Si is strong ferrite former. Cu is austenite stabilizer. Cu also increases the corrosion resistance of stainless steel. Especially in conventional PM, Cu helps sintering promoting liquid phase sintering.
- Embodiments of the invention provide a powder suitable for producing sintered duplex stainless steel, as well as the sintered stainless steel.
- the powder and the sintered stainless steel having a low or neglectable content of N. This eliminates the problem of formation of deleterious nitrides during fabrication of the sintered stainless steel.
- the sintered stainless steel is preferably produced from a compacted and sintered water-atomized powder since the low N content makes it possible to produce water-atomized powder with reasonable compressibility.
- Mo is normally present in stainless steel as it strongly promotes the resistance to both uniform and localized corrosion. Mo strongly stabilizes ferritic microstructure. At the same time Mo is prone to precipitate Mo rich "Sigma” and "Chi" phases at Ferrite- Austenite grain boundary.
- Ni promotes an austenitic microstructure and generally increases ductility and toughness. Ni has also a positive effect as it reduces the corrosion rate of stainless steels.
- Cu promotes an austenitic microstructure.
- the presence of Cu in the powder of the present invention facilitates the sintering process by enabling liquid phase sintering.
- W is expected to improve the resistance against pitting corrosion.
- Si increases strength and promotes a ferritic microstructure. It also increases oxidation resistance at high temperatures and in strongly oxidizing solutions at lower temperatures.
- B, Nb, Hf, Ti, Co may enhance the properties.
- B when added in small % may help in liquid phase sintering.
- excess B, if present, may form borides, which are deleterious to both mechanical, and corrosion properties.
- Nb and Hf when present may stabilize the microstructure by preferentially combining with carbon forming fine carbides freeing Cr for the corrosion resistance.
- Ti in stainless steels may increase the tensile strength and toughness.
- Co increases the high temperature mechanical properties.
- Elements such as C, Mn, S and P should be kept at a level as low as possible in the powder of embodiments of the present invention as they may have a negative effect to various extent on compressibility of the powder and/or mechanical and corrosion preventive properties on the sintered component.
- unavoidable impurities may be tolerated up to a content of 0.8% by weight of the powder according to the present invention.
- composition of the powder according to embodiments of the present invention is designed such that the produced powder will have fully (e.g., at least 99.5%) ferritic structure in the powder form and austenitic phase is precipitated out during sintering cycle. This will allow controlling the ratio of ferrite and austenite by adjusting the sintering parameters.
- the composition is targeted such that 5 ⁇ Ni eq ⁇ 11 and 27 ⁇ Cr eq ⁇ 38. This places the alloy in at the border of Ferritic - Duplex region on Schaeffler Diagram. At this point the alloy is almost entirely ferritic (e.g., at least 99.5%). Elements like Mo, W and Si are supersaturated in the ferritic matrix.
- the powder of embodiments of the present invention may be produced by conventional powder manufacturing processes. Such processes may encompass melting of the raw materials followed by water or gas atomization, forming a so called prealloyed powder wherein all elements are homogeneously distributed within the iron matrix.
- prealloyed powder in contrast to a premixed powder, wherein two or more powders are mixed together, is that segregation is avoided. Such segregation may cause variation in mechanical properties, corrosion resistance etc.
- the powder of embodiments of the present invention may be compacted in a conventional uniaxial compaction equipment at a compaction pressure up to 900 MPa.
- Suitable particle size distribution of the stainless steel powder to be used at conventional uniaxial compaction is such that the particle size of the powder is between 53 microns and 18 microns such that at least 80wt% of the particles are less than 53 microns and at most 20wt% of the particles are less than 18 microns.
- the powder of embodiments of the present invention may be mixed with conventional lubricants, such as, but not limited to, Acrawax, Lithium Stearate, Intralube at a content up to 1wt%.
- Other additives mixed in, up to 0.5wt% may be machinability enhancing agents such as CaF 2 , muscovite, bentonite or MnS.
- MIM Metal Injection Molding
- HIP Hot Isostatic Pressing
- extrusion additive Manufacturing techniques
- Binder Jetting Laser Powder Bed Fusion
- DMLS Direct Metal Laser Sintering
- DMD Direct Metal Deposition
- suitable particle size distribution of the stainless steel powder to be used is such that the particle size of the powder is between 26 microns and 5 microns such that at least 80wt% of the particles are less than 26 microns and at most 20wt% of the particles are less than 5 microns.
- suitable particle size distribution of the stainless steel powder to be used is such that the particle size of the powder is between 150 microns and 26 microns such that at least 80wt% of the particles are less than 150 microns and at most 20wt% of the particles are less than 26 microns.
- the particle size distribution may be measured by a conventional sieving operation according to ISO 4497:1983 or by laser diffraction (Sympatec) according to ISO 13320:1999.
- the compacted or consolidated body is subjected to a sintering process at sufficiently high temperatures in the range of 1150°C to 1450 °C, preferably at sufficiently high temperatures in the range of 1275 °C to 1400 °C for a period of time of 5 minutes to 120 minutes.
- a sintering process at sufficiently high temperatures in the range of 1150°C to 1450 °C, preferably at sufficiently high temperatures in the range of 1275 °C to 1400 °C for a period of time of 5 minutes to 120 minutes.
- other period of sintering time such as 10 minutes to 90 minutes or 15 minutes to 60 minutes may be applied.
- the sintering atmosphere may be vacuum, inert or reducing such as a hydrogen atmosphere, an atmosphere of a mixture of hydrogen and nitrogen or dissociated ammonia.
- the supersaturated elements in ferrite matrix precipitate out as an austenitic phase. Austenite will start precipitating out at the grain boundaries and with further sintering will grow and precipitate
- the composition of embodiments of the present invention should not form sigma phases or other hard and deleterious phases, e.g., Chi phase and nitrides, during cooling from an elevated temperature, irrespective of the cooling rate.
- the amount of sigma phase or other hard and deleterious phases is less than 0.5%.
- Forced cooling or quenching is thus not necessary to apply.
- forced cooling means that the sintered parts are subjected to a cooling gas at a pressure above atmospheric pressure. Quenching means that the sintered parts are submerged into a liquid cooling media.
- a microstructure as shown in Figure 1 will typically be formed containing ferrite and austenite. Presence of both phases is responsible for elevated mechanical and corrosion properties. No, or significantly limited amounts of, deleterious phases such as sigma and chi are formed during cooling which are normal for current known duplex stainless steels. As another consequence, this property will reduce or eliminate the formation of such phases during welding where the heat affected zone (HAZ) experience varying cooling rates. In another consequence, this composition will limit the precipitation of such phases during processes such as casting, extrusion, MIM, HIP and additive manufacturing.
- Embodiments of the invented alloy has shown mechanical and corrosion properties that are comparable to or exceeding the wrought and PM products manufactured with known duplex stainless steel alloys available.
- certain advantages of embodiments of this invention may include fewer tendencies to precipitate deleterious sigma and chi phases that affect the mechanical and corrosion properties. This is particularly of interest in welding. Most of the duplex stainless steel components are welded after they are formed. Welding imparts different cooling rates in different parts of HAZ. These cooling rates tend to precipitate sigma and chi phases along with nitrides due to nitrogen present in the current known alloys. Absence of these phases may eliminate the post heat treatments, which normally involve annealing at temperatures above 1200 °C followed by rapid cooling. This in most cases becomes difficult when parts are welded to a bigger structure limiting use of duplex stainless steel.
- a stainless steel powder having a particle size below 325 mesh, i.e. 95wt% of the particles passed 45 ⁇ m sieve, was mixed with 0.75wt% of Acrawax as a lubricant.
- the chemical analysis of the stainless steel powder was 0.01wt% C, 1.52wt% Si, 0.2wt% Mn, 0.013wt% P, 0.008wt% S, 24.9wt% Cr, 2.0wt% Cu, 1.3wt% Mo, 1.0wt% W, 0.05wt%N, balance Fe.
- the obtained powder mixture was pressed in a uniaxial press and compacted into transverse rapture strength (TRS) bars, according to ASTM B528-16 at a compaction pressure of 750 MPa.
- TRS transverse rapture strength
- the pressed TRS bars were then sintered in 100% hydrogen atmosphere at 1343°C with ramp rate of 7°C/minute for 45 minutes. This was followed by furnace cooling at rate 5°C/minute.
- the samples were then mounted and polished for microstructure examination.
- the polished samples were then electro-etched with 33%NaOH at 3V for 15 sec. Electro-etch with NaOH reveals the ferrite phase as tan, austenite as white (unaffected) and sigma phases in dark orange at grain boundaries within ferrite matrix.
- the microstructure observed is as shown in Figure 1 .
- the microstructure shows approximately 50/50 mixture of ferrite (tan) and austenite (white). There is no sign of any sigma phase (dark orange) in the microstructure.
- the chemical composition of the stainless steel powders are shown in table 1.
- Stainless steel melts having various chemical compositions were melted in an induction furnace, the molten metal was subjected to water stream to obtain steel powder.
- the obtained powders was then dried and screened to -325 mesh.
- the screened powder was -45 microns i.e. 95wt% of the powder particles were less than 45 microns.
- the powders were then mixed with 0.75wt% of the lubricant Acrawax.
- Table 2 shows that the stainless steel powders according to the present invention can be used for producing sintered duplex stainless steel having desired mechanical properties.
- Table 1 chemical compositions of various stainless steel powders, there production method and type of process for producing sintered samples.
- Chemical analysis [% by weight] Sample Type C Si Mn S P Cr Ni Mo W Cu O N Other Comparative DSS 329 Wrought Wrought steel 0.08 1.00 23-28 2.5-5 1-2 0.08 Comparative DSS 329 PM WA Water atomized powder, HIP 0.20 0.75 1.00 23-28 2.5-5 1-2 0.05 0.08 Comparative DSS 2205 PM GA Gas atomized powder HIP 0.03 1.00 2.00 0.020 0.030 22.0-23.0 4.5-6.5 3.0-3.5 0.75 0.14-0.20 Premix XSS DP1 PM WA Premix Water atomized powders 4 , compacted and sintered 0.03 2.00 0.10 0.006 0.008 25 5.5 1.3 1 2 0.2 0.06 Invention XSS DP1 PM WA Prealloy Water
- An embodiment of the invented powder with composition as in Example 1 was also sintered at various temperatures and atmospheres to show the effect on mechanical properties. Such data is plotted in Figure 3 .
- TRS bars as in Example 1 were produced along with bars for 316L and 434L as representatives from austenitic and ferritic grades.
- the samples were then tested for corrosion in 5% NaCl solution at room temperature per ASTM B895-16.
- the corrosion was compared by the hours takes for onset of corrosion on the samples.
- the comparative data is plotted in Figure 2 along with the UTS and YS for these samples.
- the diameter of the bubbles in the Figure 3 represents the number of hours taken for the start of the corrosion on the samples.
- the corrosion test for the invented powder was discontinued after 3700 hours as there was no sign of corrosion and it already exceeded 3 times that of 316L samples.
Description
- Embodiments of the present invention may provide a new stainless steel powder suitable for manufacturing of sintered duplex stainless steels. Embodiments of the present invention may also relate to a method for producing the sintered duplex stainless steel.
- Duplex stainless steels have been known to the industry for more than 60 years. They are widely used in heat-treated cast, wrought and gas atomized powder forms, in many applications that require a combination of high strength and high corrosion resistance. However, they are unavailable today, in the water atomized powder form for use in press and sinter applications.
- Common uses for duplex stainless steels include chemical process plants pipeline, petrochemical industry, power plants and automobiles. They are also used in food processing industry, pharmaceutical process components, paper and pulp industry, in desalination plants and in the mining industry. Duplex stainless steels are known for their high resistance to inter granular corrosion (IGC) and stress corrosion cracking (SCC) in chloride media. Chloride is severe challenge that leads to rapid corrosion media for iron-based alloys.
- High strength and high corrosion resisting properties in duplex stainless steel are believed to be acquired due to a presence of ferrite and austenite phases in equal amounts. Such structure is generally achieved by using a balance of austenite stabilizers, e.g., nickel (Ni), manganese (Mn), carbon (C), nitrogen (N), copper (Cu) and cobalt (Co), and ferrite stabilizers, e.g., chromium (Cr), silicon (Si), molybdenum (Mo), tungsten (W), titanium (Ti) and niobium (Nb).
- As mentioned previously, the high strength and high corrosion resistance of duplex stainless steel is believed to come from a balance of ferrite and austenite in the microstructure. The microstructure depends not only on the chemistry but also on the heat treatment carried out on the material. All duplex steel compositions today make use of N in the chemistry, as N is a strong austenite stabilizer. N, when present in the alloy along with Cr, poses problem of forming nitrides which are deleterious to the properties such as strength and corrosion resistance. Further, during welding duplex stainless steels, an intermetallic phase known as "Sigma" is formed in a heat affected zone (HAZ) due to slower cooling rates. This Sigma phase is a hard, supersaturated, intermetallic phase containing Cr and Mo. The area around the Sigma phase is depleted of Cr and Mo and becomes weak and less resistant to corrosion. Often duplex stainless steels need annealing and quenching process to reduce or eliminate this Sigma phase.
- In wrought or cast duplex stainless steels, the steel is solidified as ferritic steel and the austenite phase is precipitated out from ferrite during cooling of the alloy. The cooling rate is critical after casting or any heat treatment, as the cooling rate determines the percentage of austenite and any intermetallic phases precipitated within the structure.
- Although wrought duplex stainless steels, in particular 'hot rolled' duplex stainless steels, have been common in industrial use since 1930s, they were hardly used in the Powder Metallurgy industry. There are a few applications where gas atomized duplex stainless steel powders are used in hot isostatic pressed (HIP) condition. Powders produced by gas atomizing have spherical morphology. Such powders are less suitable for conventional press and sinter applications. Due to the spherical shape, they have insufficient green strength, which is required to handle green press and sinter parts. Irregular shaped powders, such as those produced with water atomization, have much higher green strength as the irregular shape of the powders tends to bind together. Currently there is no water atomized stainless steel powder available for producing sintered duplex stainless steel components. The current chemical compositions used in gas atomized powders, and also in wrought steels, use N as a major alloying element to achieve austenite-ferrite balance and achieve required mechanical strength. Inclusion of N in the powder increases the hardness of the powder reducing the compressibility in conventional press and sinter applications. This may result in reduced green density and subsequently reduced sinter density.
- There have been several attempts to develop sintered duplex stainless steels made from water atomized powders. Lawley et al1 attempted to develop equivalent grades of AISI 329 and AISI 2205 with maximum tensile strength of 578 MPa. Dobrzanski et al2 mixed ferritic and austenitic powders to produce duplex structure with tensile strength 650 MPa. The same group also studied the corrosion properties of duplex stainless steel with electrochemical method and concluded that the duplex stainless steels show better corrosion resistance than their austenitic counterpart3. Due to their high alloy content these steels are sensitive to the composition and also the processing parameters. These alloys form intermetallic phases known as sigma, chi and gamma prime which are rich in Mo, W, N, Ni and Cr and reduce both mechanical properties and corrosion properties. Sigma phase forms in a temperature range 700 °C to 1000 °C whereas Chi phase forms within
range 300 °C to 450 °C. The Gamma (austenite) phase may start forming at around 600 °C.
1 A. Lawley, E. Wagner, C.T. Schade, Advances in Powder Metallurgy and Particulate Materials 2005
2 L.A. Dobrzanski, Z. Brytan, M. Actis Grande, M. Rosso, Archives of Materials Science and Engineering, Vol 28
3 L.A. Dobrzanski, Z. Brytan, M. Actis Grande, M. Rosso, Journal of Achievements in Materials and Manufacturing Engineering, Vol 17 Iss 1-2 pp 317-320 - Typical composition of wrought duplex stainless steel is Fe with 32-23wt% Cr, 4.5-6.5wt% Ni, 2.5-3.5wt% Mo, and 0.08-0.2wt% N, such as for SAF 2205. There are numerous patents for duplex stainless steel composition close to this composition. Almost all of the duplex stainless steels rely on the N content for increased corrosion resistance and increased strength. So far the commercial uses of sintered powder metallurgy (PM) duplex stainless steels are limited to the use of gas atomized fine powders that can be used for mainly HIP process. The main obstacle in using low cost water atomized powders for conventional PM use is increased N and possibility of intermetallic and carbide precipitation due to cooling rate during the sintering. Also conventional sintering needs some wetting agents or low temperature melting constituents to increase free energy and accelerate the kinetics of austenite phase precipitation within ferritic matrix.
- In the patent literature there are some documents disclosing sintered duplex stainless steel structures.
-
SE538577C2 -
EP0167822A1 (Sumitomo) discloses a sintered stainless steel comprising a matrix phase and a dispersed phase and a process for manufacturing. The dispersed phase is an austenite metallurgical structure and is dispersed throughout the matrix phase, which is comprised of an austenitic metallurgical structure having a steel composition different from that of the dispersed phase or a ferritic-austenitic duplex stainless steel. -
JP5263199A -
EP0534864B1 (Sumitomo) discloses a sintered stainless steel having a content of N of 0.10-0.35wt% and made from gas atomized steel powder having the same chemical composition as the sintered stainless steel. - In the below mentioned published papers by Dobrzanski ET AL, the properties of sintered duplex stainless steel are discussed. Results from testing of samples made from admixed powders, forming duplex stainless steel powders, are reported.
- DOBRZANSKI L A ET AL: "Properties of vacuum sintered duplex stainless steel" JOURNAL OF MATERIALS PROCESSING TECHNOLOGY, ELSEVIER NL, vol. 162-163, May 2005 (2005-05-15), pages 282-292.
- Leszek Adam Dobrzanski ET AL: "Properties of Vacuum Sintered Duplex Stainless Steels", Advanced Materials Research, vol. 15-17, 1 February 2006 (2006-02-01), pages 828-833.
- L.A. Dobrzanski ET AL, "Properties of duplex stainless steels made by powder metallurgy", Archives of Materials Science and Engineering, Vol 28, .
- In a Doctoral Thesis by Olena Smuk, "Microstructures and Properties of Modern P/M Super Duplex Stainless Steels", ISBN 91-7283-761-6, various aspects of PM duplex and superduplex stainless steels are disclosed.
- Almost all duplex grades available have N content between 0.18- 0.40wt% in order to balance austenite-ferrite balance in the structure and increase the strength. Although N content helps the above properties, it can pose hurdles in post processing, such as heat treatment and welding operations, by forming chromium nitrides, which limits the use of duplex stainless steels in many applications. In powder form N increases the powder hardness making it less suitable for press and sinter applications.
- Embodiments of the invention overcome the problem with nitrides by avoiding the use of N in the chemistry, for example, having less than 0.10 wt% N or less than 0.07 wt% N, or less than 0.06 wt% N, or less than 0.05 wt% N, or less 0.04 wt% N, or less than 0.03 wt% N, and achieving phase balance and strength by alternative elements. Embodiments of the invention may enable production of water atomized powder with moderate compressibility for use in conventional press and sinter applications. Embodiments of this composition may also reduce precipitation of a deleterious 'Sigma' phase; irrespective of rate of cooling during sintering or annealing, mainly due to lower Mo content. Thus minimizing post sintering heat treatments necessary to eliminate "Sigma" phase and minimizing Sigma phase precipitation during welding.
- Embodiments of the composition may offer similar advantages when formed by gas atomization.
- Other than conventional powder metallurgy, embodiments of the composition yield similar properties when processed with Casting, Direct Metal Deposition and Additive Manufacturing techniques.
- One object of certain embodiments of the invention is to provide an alloy powder for conventional PM that will produce a duplex structure during a sintering cycle.
- Another object of certain embodiments of the present invention is to obtain at least 35% higher tensile strength than ferritic steels such as 430L and double the corrosion resistance than austenitic steels such as 316L.
- Still another object of certain embodiments of the present invention is to provide a method for producing a duplex sintered stainless steel without the need of post sintering heat treatment.
- The above objectives may be accomplished by the following aspects and embodiments.
- In a first aspect of the present invention there is provided a stainless steel powder comprising, or consisting of, in weight percent:
- up to 0.1wt% of C,
- 0.5-3% ofwt Si,
- up to 0.5wt% of Mn,
- 20-27wt% of Cr,
- 3-8wt% of Ni,
- 1-6wt% of Mo,
- up to 3wt% of W,
- up to 0.1wt% N,
- up to 4wt% of Cu,
- up to 0.04wt% of P,
- up to 0.04wt% of S,
- unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,
- optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,
- rest Fe.
- The unavoidable impurities do not include the listed elements of C, Si, Mn, Cr, Ni, Mo, W, N, Cu, P, S, B, Nb, Hf, Ti, or Co. Unavoidabale impurties may include impurities that cannot be controlled, or controlled with difficulty, during manufacture of steels. These can come from the raw materials used and also from the process. These include, Al, O, Mg, Ca, Ta, V, Te, or Sn. The unavoidable impurities may be up to 0.8wt%, up to 0.6wt%, up to 0.3wt%. An unavoidable impurity may be O. O may be present up to 0.6wt%, up to 0.4wt%, or up to 0.3wt%.
- In a preferred embodiment of the first aspect there is provided a stainless steel powder consisting of, in weight percent:
- up to 0.06wt% of C,
- 1-3wt% of Si,
- up to 0.3wt% of Mn,
- 23-27wt% of Cr,
- 4-7wt% of Ni,
- 1-3wt% of Mo,
- 0.8-1.5wt% of W,
- up to 0.07wt% N,
- 1-3wt% of Cu,
- up to 0.04wt% of P,
- up to 0.03wt% of S,
- unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,
- optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,
- rest Fe.
- In another preferred embodiment of the first aspect there is provided a stainless steel powder comprising in weight percent:
- up to 0.03wt% of C,
- 1.5-2.5wt% of Si,
- up to 0.3wt% of Mn,
- 24-26wt% of Cr,
- 5-7wt% of Ni,
- 1-1.5wt% of Mo,
- 1-1.5wt% of W,
- up to 0.06wt% N,
- 1-3wt% of Cu,
- up to 0.02wt% of P,
- up to 0.015wt% of S,
- unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,
- optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,
- rest Fe.
- In embodiments of the first aspect the powder is ferritic. For example, 99.5% ferritic. Slight amounts of austenite, e.g., up to 0.5% may be tolerated.
- In embodiments according to the first aspect the powder is produced by water atomization.
- In embodiments of the first aspect the powder is produced by gas atomization.
- In embodiments of the first aspect the particle size of the powder is between 53 microns and 18 microns such that at least 80wt% of the particles are less than 53 microns and at most 20wt% of the particles are less than 18 microns.
- In embodiments of the first aspect the particle size of the powder is between 26 microns and 5 microns such that at least 80wt% of the particles are less than 26 microns and at most 20wt% of the particles are less than 5 microns.
- In embodiments of the first aspect the particle size of the powder is between 150 microns and 26 microns such that at least 80wt% of the particles are less than 150 microns and at most 20wt% of the particles are less than 26 microns.
- In a second aspect of the present invention there is provided a method for producing a sintered stainless steel comprising the steps of:
- providing a stainless steel powder according to the first aspect,
- optionally mixing the stainless steel powder with a lubricant and optionally other additives,
- subjecting the stainless steel powder or the mixture to a consolidation process forming a green component,
- subjecting the compacted green component to a sintering step in an inert or reducing atmosphere or in vacuum at a temperature between 1150 °C to 1450 °C, preferably at a temperature between 1275 °C to 1400 °C for a period of time of 5 minutes to 120 minutes ,
- subjecting the sintered component to a cooling step down to ambient temperature.
- Examples of an inert atmosphere include nitrogen, argon, and vacuum with argon backfill.
- An example of a reducing atmosphere is a hydrogen atmosphere, an atmosphere of a mixture of hydrogen and nitrogen, or an atmosphere of dissociated ammonia. In limited examples, carbon dioxide or carbon monoxide atmospheres may be used.
- In embodiments of the second aspect said consolidation process includes the steps of:
- uniaxial compaction at a compaction pressure of up to 900 MPa in a die to form a green component,
- ejecting the obtained compacted green component from the die.
- In embodiments of the second aspect said consolidation process includes one of: Metal Injection Molding (MIM), Hot Isostatic Pressing (HIP) or Additive Manufacturing techniques such as Binder Jetting, Laser Powder Bed Fusion (L-PBF), Direct Metal Laser Sintering (DMLS) or Direct Metal Deposition (DMD).
- In embodiments of the second aspect forced cooling or quenching is excluded from the cooling step.
- The effect of common alloying elements in stainless steels is well known. Cr is a major element in stainless steels which forms a Cr2O3 layer on the surface which then prevents further oxygen passing the layer, therefore providing an increased corrosion resistance. Ni is another major element which affects the properties of stainless steel. Ni increases the strength and toughness of the steel and also when present with Cr, enhances the corrosion resistance. Mo and W both impart the strength and toughness when present along with Ni. Mo also enhances the corrosion resistance along with Cr and Ni. Si acts as deoxidizer preventing O combining in the steel during melting and also Si is strong ferrite former. Cu is austenite stabilizer. Cu also increases the corrosion resistance of stainless steel. Especially in conventional PM, Cu helps sintering promoting liquid phase sintering.
Embodiments of the invention provide a powder suitable for producing sintered duplex stainless steel, as well as the sintered stainless steel. The powder and the sintered stainless steel having a low or neglectable content of N. This eliminates the problem of formation of deleterious nitrides during fabrication of the sintered stainless steel. The sintered stainless steel is preferably produced from a compacted and sintered water-atomized powder since the low N content makes it possible to produce water-atomized powder with reasonable compressibility.
Mo is normally present in stainless steel as it strongly promotes the resistance to both uniform and localized corrosion. Mo strongly stabilizes ferritic microstructure. At the same time Mo is prone to precipitate Mo rich "Sigma" and "Chi" phases at Ferrite- Austenite grain boundary. These are deleterious phases and affect strength and corrosion resistance adversely. However, due to lower Mo content in embodiments of the powder of the present invention, the possibility of forming sigma phase at any cooling rate is reduced, eliminating or reducing the need for the post processing heat treatment of annealing. This also means that the sigma phase will not likely form during welding operation, which is a common fabrication process for duplex stainless steels. - Cr gives stainless steels their basic corrosion resistance and increases the resistance against high temperature corrosion.
- Ni promotes an austenitic microstructure and generally increases ductility and toughness. Ni has also a positive effect as it reduces the corrosion rate of stainless steels.
- Cu promotes an austenitic microstructure. The presence of Cu in the powder of the present invention facilitates the sintering process by enabling liquid phase sintering.
- W is expected to improve the resistance against pitting corrosion.
- Si increases strength and promotes a ferritic microstructure. It also increases oxidation resistance at high temperatures and in strongly oxidizing solutions at lower temperatures.
- When present in the powder according to certain embodiments of the present invention B, Nb, Hf, Ti, Co may enhance the properties. B when added in small % may help in liquid phase sintering. However, excess B, if present, may form borides, which are deleterious to both mechanical, and corrosion properties. Nb and Hf when present may stabilize the microstructure by preferentially combining with carbon forming fine carbides freeing Cr for the corrosion resistance. Ti in stainless steels may increase the tensile strength and toughness. Co increases the high temperature mechanical properties.
- Elements such as C, Mn, S and P should be kept at a level as low as possible in the powder of embodiments of the present invention as they may have a negative effect to various extent on compressibility of the powder and/or mechanical and corrosion preventive properties on the sintered component.
- Other elements, here designated as unavoidable impurities, may be tolerated up to a content of 0.8% by weight of the powder according to the present invention.
- The composition of the powder according to embodiments of the present invention is designed such that the produced powder will have fully (e.g., at least 99.5%) ferritic structure in the powder form and austenitic phase is precipitated out during sintering cycle. This will allow controlling the ratio of ferrite and austenite by adjusting the sintering parameters.
-
-
- The composition is targeted such that 5 < Nieq < 11 and 27 < Creq <38. This places the alloy in at the border of Ferritic - Duplex region on Schaeffler Diagram. At this point the alloy is almost entirely ferritic (e.g., at least 99.5%). Elements like Mo, W and Si are supersaturated in the ferritic matrix.
- The powder of embodiments of the present invention may be produced by conventional powder manufacturing processes. Such processes may encompass melting of the raw materials followed by water or gas atomization, forming a so called prealloyed powder wherein all elements are homogeneously distributed within the iron matrix. A major advantage with a prealloyed powder in contrast to a premixed powder, wherein two or more powders are mixed together, is that segregation is avoided. Such segregation may cause variation in mechanical properties, corrosion resistance etc.
- When used for the production of sintered components, the powder of embodiments of the present invention may be compacted in a conventional uniaxial compaction equipment at a compaction pressure up to 900 MPa.
- Suitable particle size distribution of the stainless steel powder to be used at conventional uniaxial compaction is such that the particle size of the powder is between 53 microns and 18 microns such that at least 80wt% of the particles are less than 53 microns and at most 20wt% of the particles are less than 18 microns. Before compaction, the powder of embodiments of the present invention may be mixed with conventional lubricants, such as, but not limited to, Acrawax, Lithium Stearate, Intralube at a content up to 1wt%. Other additives mixed in, up to 0.5wt%, may be machinability enhancing agents such as CaF2, muscovite, bentonite or MnS.
- Other methods of consolidation techniques may be utilized such as Metal Injection Molding (MIM), Hot Isostatic Pressing (HIP), extrusion or Additive Manufacturing techniques such as Binder Jetting, Laser Powder Bed Fusion (L-PBF), Direct Metal Laser Sintering (DMLS) or Direct Metal Deposition (DMD)
- In a MIM process, suitable particle size distribution of the stainless steel powder to be used is such that the particle size of the powder is between 26 microns and 5 microns such that at least 80wt% of the particles are less than 26 microns and at most 20wt% of the particles are less than 5 microns.
- In a HIP or extrusion process suitable particle size distribution of the stainless steel powder to be used is such that the particle size of the powder is between 150 microns and 26 microns such that at least 80wt% of the particles are less than 150 microns and at most 20wt% of the particles are less than 26 microns.
- The particle size distribution may be measured by a conventional sieving operation according to ISO 4497:1983 or by laser diffraction (Sympatec) according to ISO 13320:1999.
- After compaction or consolidation, the compacted or consolidated body is subjected to a sintering process at sufficiently high temperatures in the range of 1150°C to 1450 °C, preferably at sufficiently high temperatures in the range of 1275 °C to 1400 °C for a period of time of 5 minutes to 120 minutes. Depending of shape and size of parts to be sintered, other period of sintering time such as 10 minutes to 90 minutes or 15 minutes to 60 minutes may be applied. The sintering atmosphere may be vacuum, inert or reducing such as a hydrogen atmosphere, an atmosphere of a mixture of hydrogen and nitrogen or dissociated ammonia. During the sintering process, the supersaturated elements in ferrite matrix precipitate out as an austenitic phase. Austenite will start precipitating out at the grain boundaries and with further sintering will grow and precipitate within the grain itself.
- In contrast to other known duplex stainless steel materials, the composition of embodiments of the present invention should not form sigma phases or other hard and deleterious phases, e.g., Chi phase and nitrides, during cooling from an elevated temperature, irrespective of the cooling rate. For example, the amount of sigma phase or other hard and deleterious phases is less than 0.5%. Forced cooling or quenching is thus not necessary to apply. In this context forced cooling means that the sintered parts are subjected to a cooling gas at a pressure above atmospheric pressure. Quenching means that the sintered parts are submerged into a liquid cooling media.
- A microstructure as shown in
Figure 1 will typically be formed containing ferrite and austenite. Presence of both phases is responsible for elevated mechanical and corrosion properties. No, or significantly limited amounts of, deleterious phases such as sigma and chi are formed during cooling which are normal for current known duplex stainless steels. As another consequence, this property will reduce or eliminate the formation of such phases during welding where the heat affected zone (HAZ) experience varying cooling rates. In another consequence, this composition will limit the precipitation of such phases during processes such as casting, extrusion, MIM, HIP and additive manufacturing. - Embodiments of the invented alloy has shown mechanical and corrosion properties that are comparable to or exceeding the wrought and PM products manufactured with known duplex stainless steel alloys available.
- In summary, certain advantages of embodiments of this invention may include fewer tendencies to precipitate deleterious sigma and chi phases that affect the mechanical and corrosion properties. This is particularly of interest in welding. Most of the duplex stainless steel components are welded after they are formed. Welding imparts different cooling rates in different parts of HAZ. These cooling rates tend to precipitate sigma and chi phases along with nitrides due to nitrogen present in the current known alloys. Absence of these phases may eliminate the post heat treatments, which normally involve annealing at temperatures above 1200 °C followed by rapid cooling. This in most cases becomes difficult when parts are welded to a bigger structure limiting use of duplex stainless steel.
-
-
Figure 1 shows the microstructure of invented sintered stainless steel, austenite and ferrite phases are present in equal proportions in as sintered condition, black spots are porosity. -
Figure 2 discloses a comparison of ultimate tensile strength (UTS) and corrosion properties of the invented sintered stainless steel compared to alloy to 300 and 400 alloys -
Figure 3 shows a comparison of mechanical properties of the invented sintered stainless steel at different sintering conditions - A stainless steel powder, having a particle size below 325 mesh, i.e. 95wt% of the particles passed 45µm sieve, was mixed with 0.75wt% of Acrawax as a lubricant. The chemical analysis of the stainless steel powder was 0.01wt% C, 1.52wt% Si, 0.2wt% Mn, 0.013wt% P, 0.008wt% S, 24.9wt% Cr, 2.0wt% Cu, 1.3wt% Mo, 1.0wt% W, 0.05wt%N, balance Fe.
- The obtained powder mixture was pressed in a uniaxial press and compacted into transverse rapture strength (TRS) bars, according to ASTM B528-16 at a compaction pressure of 750 MPa. The pressed TRS bars were then sintered in 100% hydrogen atmosphere at 1343°C with ramp rate of 7°C/minute for 45 minutes. This was followed by furnace cooling at
rate 5°C/minute. The samples were then mounted and polished for microstructure examination. The polished samples were then electro-etched with 33%NaOH at 3V for 15 sec. Electro-etch with NaOH reveals the ferrite phase as tan, austenite as white (unaffected) and sigma phases in dark orange at grain boundaries within ferrite matrix. The microstructure observed is as shown inFigure 1 . The microstructure shows approximately 50/50 mixture of ferrite (tan) and austenite (white). There is no sign of any sigma phase (dark orange) in the microstructure. The black spots are porosity in the sample. - Various stainless steel powders according to embodiments of the invention, and as comparative samples, were produced by water atomizing. The chemical composition of the stainless steel powders are shown in table 1. Stainless steel melts having various chemical compositions were melted in an induction furnace, the molten metal was subjected to water stream to obtain steel powder. The obtained powders was then dried and screened to -325 mesh. The screened powder was -45 microns i.e. 95wt% of the powder particles were less than 45 microns. The powders were then mixed with 0.75wt% of the lubricant Acrawax.
- In order to test the mechanical properties i.e. ultimate tensile strength (UTS), yield strength (YS) and elongation, TS samples (dog bone) per ASTM B925-15 were pressed with a compaction pressure of 750 MPa. The bars were then sintered as mentioned in Example 1. The sintered bars were then tested for mechanical properties per ASTM E8/E8M-16a. Metallographic examination was also conducted in order to establish the ratio between austenite and ferrite in sintered samples. The test results are shown in table 2 in comparison with published data from samples of known duplex stainless steels in wrought, (DSS 329 Wrought), and gas atomized and hipped conditions (DSS 329 PM GA).
- Table 2 shows that the stainless steel powders according to the present invention can be used for producing sintered duplex stainless steel having desired mechanical properties.
Table 1, chemical compositions of various stainless steel powders, there production method and type of process for producing sintered samples. Chemical analysis [% by weight] Sample Type C Si Mn S P Cr Ni Mo W Cu O N Other Comparative DSS 329 Wrought Wrought steel 0.08 1.00 23-28 2.5-5 1-2 0.08 Comparative DSS 329 PM WA Water atomized powder, HIP 0.20 0.75 1.00 23-28 2.5-5 1-2 0.05 0.08 Comparative DSS 2205 PM GA Gas atomized powder HIP 0.03 1.00 2.00 0.020 0.030 22.0-23.0 4.5-6.5 3.0-3.5 0.75 0.14-0.20 Premix XSS DP1 PM WA Premix Water atomized powders4, compacted and sintered 0.03 2.00 0.10 0.006 0.008 25 5.5 1.3 1 2 0.2 0.06 Invention XSS DP1 PM WA Prealloy Water atomized powder, prealloyed compacted and sintered 0.01 1.52 0.20 0.013 0.008 24.9 5.5 1.3 1 2 0.1 5 0.05 Invention XSS DP1-1 Water atomized powder, prealloyed compacted and sintered 0.03 1.97 0.10 0.007 0.012 23.4 5.1 1.2 0.9 1.9 0.1 3 0.05 Invention XSS DP1-2 Water atomized powder, prealloyed compacted and sintered 0.03 2.12 0.20 0.007 0.012 26.1 5.2 1.3 0.9 3 0.1 5 0.02 Invention XSS DP1-3 Water atomized powder, prealloyed compacted and sintered 0.03 1.94 0.20 0.008 0.013 25.1 5.6 1.2 0.8 2 0.15 0.02 0.58 Nb Comparative XSS DP1-4 Water atomized powder, prealloyed compacted and sintered 0.03 2.14 0.20 0.009 0.015 22.3 5.2 1.3 0.9 1.9 0.1 6 0.06 0.6 Sn 4 Premix of 316L, 434L and elemental powders of Si, W and Cu. Table 2, mechanical properties and metallographic structure for sintered samples produced from stainless steel powders according to table 1. Mechanical Properties Sample Type Sintering time [minutes] TS [Mpa] YS [Mpa] TRS [Mpa] Elongation [%] % austenite in ferrite matrix Comparative DSS 329 Wrought Wrought steel Annealed 725 550 25 ∼50 Comparative DSS 329 PM WA Water atomized powder, HIP 45 523 460 180 7 0 Comparative DSS 2205 PM GA Gas atomized powder, HIP 45 578 427 200 11 ∼50 Comparative XSS DP1 PM WA Premix Water atomized powders5, compacted and sintered 45 720 700 220 2.5 ∼35 Invention XSS DP1 PM WA Preallov Water atomized powder, prealloyed compacted and sintered 45 776 617 278 8.6 ∼60 Invention XSS DP1-1 Water atomized powder, prealloyed compacted and sintered 45 727 504 275 11.0 ∼50 Invention XSS DP1-2 Water atomized powder, prealloyed compacted and sintered 45 809 745 265 2.5 ∼50 Invention XSS DP1-3 Water atomized powder, prealloyed compacted and sintered 45 843 691 257 6.5 ∼45 Comparative XSS DP1-4 Water atomized powder, prealloyed compacted and sintered 45 749 743 218 0.5 ∼10 5 Premix of 316L, 434L and elemental powders of Si, W and Cu. - An embodiment of the invented powder with composition as in Example 1 was also sintered at various temperatures and atmospheres to show the effect on mechanical properties. Such data is plotted in
Figure 3 . - In order to perform corrosion test, TRS bars as in Example 1 were produced along with bars for 316L and 434L as representatives from austenitic and ferritic grades. The samples were then tested for corrosion in 5% NaCl solution at room temperature per ASTM B895-16. The corrosion was compared by the hours takes for onset of corrosion on the samples. The comparative data is plotted in
Figure 2 along with the UTS and YS for these samples. The diameter of the bubbles in theFigure 3 represents the number of hours taken for the start of the corrosion on the samples. The corrosion test for the invented powder was discontinued after 3700 hours as there was no sign of corrosion and it already exceeded 3 times that of 316L samples.
Claims (11)
- A prealloyed ferritic stainless steel powder comprising:up to 0.1wt% of C,0.5-3wt% of Si,up to 0.5wt% of Mn,20-27wt% of Cr,3-8wt% of Ni,1-6wt% of Mo,up to 3wt% of W,up to 0.1wt% N,up to 4wt% of Cu,up to 0.04wt% of P,up to 0.04wt% of S,unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,rest Fe.
- A prealloyed ferritic stainless steel powder according to claim 1 comprising:up to 0.06wt% of C,1-3wt% of Si,up to 0.3wt% of Mn,23-27wt% of Cr,4-7wt% of Ni,1-3wt% of Mo,0.8-1.5wt% of W,up to 0.07wt% N,1-3wt% of Cu,up to 0.03wt% of P,up to 0.03wt% of S,unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,rest Fe.
- A prealloyed ferritic stainless steel powder according to claim 1 comprising:up to 0.03wt% of C,1.5-2.5wt% of Si,up to 0.3wt% of Mn,24-26wt% of Cr,5-7wt% of Ni,1-1.5wt% of Mo,1-1.5wt% of W,up to 0.06wt% N,1-3wt% of Cu,up to 0.02wt% of P,up to 0.015wt% of S,unavoidable impurities up to 0.8wt%, whereof O may be up to 0.6wt%,optionally one or more of up to 0.004wt% B, up to 1wt% Nb, up to 0.5wt% Hf, up to 1wt% Ti, up to 1wt% Co,rest Fe.
- A prealloyed ferritic stainless steel powder according to any of claims 1 to 3 wherein the stainless steel powder is produced by water atomization.
- A prealloyed ferritic stainless steel powder according to any of claims 1 to 3 wherein the stainless steel powder is produced by gas atomization.
- A prealloyed ferritic stainless steel powder according to any of claims 1 to 3 wherein the particle size of the powder is between 53 microns and 18 microns such that at least 80% of the particles are less than 53 microns and at most 20% of the particles are less than 18 microns measured by laser diffraction according to ISO 13320:1999.
- A prealloyed ferritic stainless steel powder according to any of claims 1 to 3 wherein the particle size of the powder is between 26 microns and 5 microns such that at least 80% of the particles are less than 26 microns and at most 20% of the particles are less than 5 microns measured by laser diffraction according to ISO 13320:1999.
- A prealloyed ferritic stainless steel powder according to any of claims 1 to 3 wherein the particle size of the powder is between 150 microns and 26 microns such that at least 80% of the particles are less than 150 microns and at most 20% of the particles are less than 26 microns measured by laser diffraction according to ISO 13320:1999.
- A method for producing a sintered duplex stainless steel comprising the steps of:- providing a stainless steel powder according to any of claims 1 to 8,- optionally mixing the stainless steel powder with a lubricant and optionally other additives,- subjecting the stainless steel powder or the mixture to a consolidation process forming a green component,- subjecting the consolidated green component to a sintering step in an inert or reducing atmosphere or in vacuum at a temperature between 1150 °C to 1450 °C, preferably at a temperature between 1275 °C to 1400 °C for a period of time of 5 minutes to 120 minutes ,- subjecting the sintered component to a cooling step down to ambient temperature.
- A method for producing a sintered duplex stainless according to claim 9 wherein the consolidation process includes:- uniaxial compaction at a compaction pressure of up to 900 MPa in a die to form a green component,- ejecting the obtained compacted green component from the die.
- A method for producing a sintered duplex stainless steel according to claim 9 wherein the consolidation process includes one of:
Metal Injection Molding (MIM), Hot Isostatic Pressing (HIP), Additive Manufacturing techniques such as Binder Jetting.
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TW201833346A (en) | 2018-09-16 |
EP3551775B1 (en) | 2021-06-23 |
CN110168122A (en) | 2019-08-23 |
JP2020509167A (en) | 2020-03-26 |
TWI760395B (en) | 2022-04-11 |
BR112019011395B1 (en) | 2023-10-31 |
DK3333275T3 (en) | 2021-02-08 |
WO2018104179A1 (en) | 2018-06-14 |
ZA201903576B (en) | 2020-12-23 |
EP3551775A1 (en) | 2019-10-16 |
US20240117478A1 (en) | 2024-04-11 |
KR102408835B1 (en) | 2022-06-13 |
ES2848378T3 (en) | 2021-08-09 |
RU2753717C2 (en) | 2021-08-20 |
PL3333275T3 (en) | 2021-05-17 |
BR112019011395A2 (en) | 2019-10-15 |
AU2017370993B2 (en) | 2023-05-11 |
KR20190092493A (en) | 2019-08-07 |
JP7028875B2 (en) | 2022-03-02 |
EP3333275A1 (en) | 2018-06-13 |
US20190309399A1 (en) | 2019-10-10 |
CA3046282A1 (en) | 2018-06-14 |
AU2017370993A1 (en) | 2019-06-20 |
MX2019006609A (en) | 2019-08-01 |
RU2019121005A (en) | 2021-01-11 |
RU2019121005A3 (en) | 2021-04-19 |
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