CA1086990A - Low alloy steel for nuclear applications - Google Patents
Low alloy steel for nuclear applicationsInfo
- Publication number
- CA1086990A CA1086990A CA000290035A CA290035A CA1086990A CA 1086990 A CA1086990 A CA 1086990A CA 000290035 A CA000290035 A CA 000290035A CA 290035 A CA290035 A CA 290035A CA 1086990 A CA1086990 A CA 1086990A
- Authority
- CA
- Canada
- Prior art keywords
- weight
- steel
- sulphur
- vanadium
- carbon
- 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
- 229910000851 Alloy steel Inorganic materials 0.000 title 1
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 86
- 239000010959 steel Substances 0.000 claims abstract description 86
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 13
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 11
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 11
- 239000005864 Sulphur Substances 0.000 claims abstract description 11
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 11
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 239000011733 molybdenum Substances 0.000 claims abstract description 10
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 10
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 239000010703 silicon Substances 0.000 claims abstract description 9
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 239000011574 phosphorus Substances 0.000 claims abstract description 8
- 229910052718 tin Inorganic materials 0.000 claims abstract description 8
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 7
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims abstract description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 239000010949 copper Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052684 Cerium Inorganic materials 0.000 claims description 12
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 claims description 12
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 239000011651 chromium Substances 0.000 claims description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000011572 manganese Substances 0.000 claims description 3
- 230000007704 transition Effects 0.000 abstract description 30
- 230000005855 radiation Effects 0.000 abstract description 10
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract description 7
- 238000003466 welding Methods 0.000 abstract description 6
- 235000016768 molybdenum Nutrition 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 description 14
- 239000000203 mixture Substances 0.000 description 13
- 238000010791 quenching Methods 0.000 description 11
- 230000000171 quenching effect Effects 0.000 description 11
- 241001058146 Erium Species 0.000 description 7
- 230000009471 action Effects 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 5
- 238000005496 tempering Methods 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 241000905957 Channa melasoma Species 0.000 description 1
- 101100268840 Danio rerio chrna1 gene Proteins 0.000 description 1
- PWHVEHULNLETOV-UHFFFAOYSA-N Nic-1 Natural products C12OC2C2(O)CC=CC(=O)C2(C)C(CCC2=C3)C1C2=CC=C3C(C)C1OC(O)C2(C)OC2(C)C1 PWHVEHULNLETOV-UHFFFAOYSA-N 0.000 description 1
- DPWPWRLQFGFJFI-UHFFFAOYSA-N Pargyline Chemical compound C#CCN(C)CC1=CC=CC=C1 DPWPWRLQFGFJFI-UHFFFAOYSA-N 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- JEGUKCSWCFPDGT-UHFFFAOYSA-N h2o hydrate Chemical compound O.O JEGUKCSWCFPDGT-UHFFFAOYSA-N 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- -1 phospho Chemical class 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
STEEL
Abstract of the Disclosure The steel according to the invention consists of 0.12--0.20% by weight of carbon, 0.15-0.37% by weight of silicon, 0.3-0.8% by weight of manganese, 1.6-2.7% by weight of chromi-um, 0.8-2.0% by weight of nickel, 0.5-1.0% by weight of molyb-denum, 0.05-0.15% by weight of vanadium, 0.002-0,08% by weight of zerium, 0.01-0.10% by weight of copper, 0.0005-0.009% by weight of antimony, 0.0005-0.009% by weight of tin, 0.001-0.02, by weight of sulphur, 0.002-0.02 % by weight of phosphorus, 96.246-92.862% by weight of iron.
The steel exhibits improved resistance against neutron radiation. At 300°C and neutron fluence of 1.1020 neutr./cm2, the transition embrittlement temperature increases by no more than 50°C. The steel is designed for application in structural members having a wall thickness of up to 650 mm and has ultima-te strength
Abstract of the Disclosure The steel according to the invention consists of 0.12--0.20% by weight of carbon, 0.15-0.37% by weight of silicon, 0.3-0.8% by weight of manganese, 1.6-2.7% by weight of chromi-um, 0.8-2.0% by weight of nickel, 0.5-1.0% by weight of molyb-denum, 0.05-0.15% by weight of vanadium, 0.002-0,08% by weight of zerium, 0.01-0.10% by weight of copper, 0.0005-0.009% by weight of antimony, 0.0005-0.009% by weight of tin, 0.001-0.02, by weight of sulphur, 0.002-0.02 % by weight of phosphorus, 96.246-92.862% by weight of iron.
The steel exhibits improved resistance against neutron radiation. At 300°C and neutron fluence of 1.1020 neutr./cm2, the transition embrittlement temperature increases by no more than 50°C. The steel is designed for application in structural members having a wall thickness of up to 650 mm and has ultima-te strength
Description
~08699~
The present inventiorl rela-t~s to -the ~etal production, and more particularly, to the steel production.
Field of the Invention The steel according to the invention is to be used in the manufacture o~ casings of energy and propulsion nuclear reactors operating under high pressure of heat carrier.
Background o~ the Invention Known in the art is steel consisting o~ 0.13% by weight o~ carbon, 0.15-0.30% by weight o~ silicon, 0.30-0.55% by weight o~ manganese, 1-1.5% by weight o~ chromium, 1.0~1.6~o by weight o-~ nickel, 0.5-0~7% by weight o~ molybdenum, 0.01-0.10~o by weight of vanadium, 0.02-0.04% by weight of ~erium, sulphur and phosphorus in a quantity o~ less than or equal to 0.020% by weight, iron- the balance. Such steel possesses high mechanical properties (yield strength o~ 50 kg/mrn2);
however1it is prone to embrittlement under -the action o~ neut-ron radiation (transition em~rittlement temperature Tk incre-ases by 120-160C with neutron fluence of abou-t 1.102~ neutr./
/cm ). In addition, the prior art steel can~ot be used ~or making structural members having a wall thicX~ess exceeding 400 mm due to insu~ficient hardening depth.
Enow~ in the art is also steel consisting o~ 0.11-0.25%
by weight of carbon, 0.1?-0.37% by weigh-t o~ silicon, 0.3-0.6%
by weight of manganese, 2-3% by weight o~ chromium, 0.6-0.8%
by weight of molybdenum, 0.25-0 35% by weight o~ vanadium, .
The present inventiorl rela-t~s to -the ~etal production, and more particularly, to the steel production.
Field of the Invention The steel according to the invention is to be used in the manufacture o~ casings of energy and propulsion nuclear reactors operating under high pressure of heat carrier.
Background o~ the Invention Known in the art is steel consisting o~ 0.13% by weight o~ carbon, 0.15-0.30% by weight o~ silicon, 0.30-0.55% by weight o~ manganese, 1-1.5% by weight o~ chromium, 1.0~1.6~o by weight o-~ nickel, 0.5-0~7% by weight o~ molybdenum, 0.01-0.10~o by weight of vanadium, 0.02-0.04% by weight of ~erium, sulphur and phosphorus in a quantity o~ less than or equal to 0.020% by weight, iron- the balance. Such steel possesses high mechanical properties (yield strength o~ 50 kg/mrn2);
however1it is prone to embrittlement under -the action o~ neut-ron radiation (transition em~rittlement temperature Tk incre-ases by 120-160C with neutron fluence of abou-t 1.102~ neutr./
/cm ). In addition, the prior art steel can~ot be used ~or making structural members having a wall thicX~ess exceeding 400 mm due to insu~ficient hardening depth.
Enow~ in the art is also steel consisting o~ 0.11-0.25%
by weight of carbon, 0.1?-0.37% by weigh-t o~ silicon, 0.3-0.6%
by weight of manganese, 2-3% by weight o~ chromium, 0.6-0.8%
by weight of molybdenum, 0.25-0 35% by weight o~ vanadium, .
-2-':.
101~699~
a quantity of sulphur and phosphorLIs less than or equal to 0~025Yo by weiOht, iron- the balance. ~he steel exhiGit~ high strength (yield strength equal to or less tha~ 55 kg/mm2) and good resistance against radiation (an increase in the transiti~
on embrittlement temperature ~ ~k is less t~an or equal to 60C with a ~eutron fluence of about 1.102 neutr /cm2). ~his steel ca~not, however9 be used for the manufacture of structu-ral members with a wall thickness exceeding 400 mm, and u~elding o~ such members is associated with difficulties because an accompanying heating at 300-350C and immediate temperin~
are required after the welding.
~nown i~ the art is steel consisting o~ 0.25% by weight of carbon, 0~15-0.3% by weight of silicon, 0~5-1~5% by weight of manganese, 0.4-0.7~0 by weight o~ nickel, 0~45-0.6~o by weight of molybdenum, 0.04% by weight of sulphur, 0.035% by weight o~ phosphorus, iron- the balance. ~his steel fea-tures ~ood manufacturing properties and weldability, but is charac-terized b~ low strength (yield strength equal to or less than 35 kg/~2)~ is embri~tled under the action o~ neutron radiati-o~ ( d ~=10~-2~0C with a ~luence o~ neutrons o~ about 5.~lo19 neutr. /cm2).
Also known in the art is s~eel containing 0~20% by weight o~ carbon, 0.020-0.3% by weight of silicon, 0.4% by weight of manganese, 1~5-~.0% by weight o~ chromium, 3-4% by weight of ~ickel, 0.45-0.60% by weight of molybdenum, 0.03% by weight of vanadium, ~ 0.02% by weight of sulphur and phosphorus, iron- the balance.
. .:.. ' . ,~ ' ,,. :: . ';' , ., , ; ,' , . . . . .
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L08~;99~ ~
~ his steel exhiDi-ts high stre~th (yield stre~gth e~ual to or less than 60 kg~/mm2) and high toughness, it is good ~or welding. Howeverg this s-teel is prone to embrittlement A under heat and radiation action ( ~ Tk=1~-150C with a fluence of neutrons o~ about 5.1019 neutr./cm2).
It is an object o~ the invention to eliminate -the above disadvantages r The main object of the invention i~ to pxovide steel to be used in the manu~acture o~ casin~s of neuclear reactors which exhibits an improved resistance a$ainst the action of neutxon radiation.
Another object of the invention is to provide steel which exhibits an improved hardening depth.
~ he invention consists in the provision of steel conta-ning such components and in such proportions as to improve -~
t~e resistance of steel against the action o~ neutron radiation ;
and increase hardening depth of the steel.
Summary o~ the Invention The above objects are accomplished by that steel contai-ning carbon9 silicon9 manganese, ohromium, nickel, molybdenum, vanadium, ~erium, sulphur, phospho~us and iron, according to the invehtion, additionally contains copper9 antimony and ti~ the above-mentioned component~ being used in the ~ollo-wing quantities, in % by weight:
- . - . " . : . .. ~ .. .. ; : ~ ,: :
; . . . .... .....
, ~
',., , , ' ~ ~ ' ., ;,~
.
:~D86990 carbon 0.12-0.20 silicon 0.15-0.37 manganese 0.3-0.8 chromiu~ 1.6-2.7 nickel 0.8-2.0 molybdenum o.5_~o vanadium 0.05_0.15 ~erium 0.002-0.08 sulphur 0,001-~ 02 phosphorus 0.oo2-o.o2 copper 0.01-0.1 ~ntimony o.ooo5_o,009 tin 0-0005-0.009 iron the balance Accordi~g to the invention, a total content of antimony and tin i~ the steel is preferably from 0~001 to 0.01% by weight.
Due to the present invention it is now possible to provi-de steel exhibiti~g an improved resistance against neutron radiation. At 300C and fluence of neutro~s of 1.102 neutr./cm (~ ~ 0.5 MeV), the transition embrittlemRnt temperature is increased by ~o more than 50C. ~he steel can be u~ed i~
structural members wi~h a wall thickness of up to 650 mm and has an ultimate strength ~ ab 350C of at least 55 kgf/mm2.
The steel does not require immediate tempering a~ter welding.
~urther objects and advantages of the inve~tion will become apparent from the following detailed description of ~, 5 ,: :
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' ~:
, . -, , . . . . ... . .. . . - . ~ . . . . . ~
~, . ., i :
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... . . . . ... . . . . . . .. . . .. . . .. . .
8699~
the steel and pre~erred embodiments o-f the invention.
Detailed Description The steel according to the invention has the following coraposition: 0.12-0.2~)% by weight of carbon, 0.15-0.37% by weight of silicon, 0.3-0.8% by weight of manganese, 1.6-2.7%
by weight of chromium, 0.8-2.0% by weight of nickel, 0.5-1.0~o by wei~ht o~ molybdenum, 0.05-0.15% by wei~ht of vanadium, 0.002-0.08% by weight of ~erium, 0.01-0.10% by weight of copper, 0.0005-0.009~0 by weight of antimony, 0.0005-0 009%
b~ weight of tin, 0.001-0.02% b~ weight of sulphur, 0 002-0.02( % by weight of phosphorus, 96~246-92.862% by weight of iron.
~ he above-mentioned contents of copper, antimony and tin, in combination, impart to the steel according to the invention resistance against radiation-induced embrittlement.
Carbon content in the steel is from 0.12 to 0.20% by ~eight. With a carbon content in the steel at least 0.12% by w~ight, time resistance of at least 62 kgf/mm2 is ensured at 20C. For good welding properties of the steel, carbon content is not to exceed 0.20% by weight.
Silicon and manganese are used in quantities providing for complete desoxidation o~ steel. ~he upper limit of their content is de~ined by the above-mentioned values to prevent lowering of toughness of the steel.
Chromium content of at least 1.6~o by weight provides for requlred strer~th ,rd toughnsss Or the stssl with a wall . .
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8~g9 tliickness o~ up to ~5~ mrL. ~ith chromium content no~ e~oeedir,~
2.7~o b,y wei~h-t, ~ood ~eld.3bility of the steel i_ ensured.
Niclcel is used in the steel as the elemen-t which is most favourable for improving hardenin~ depth and toughness of steel. However, nickel content in steel is not to exceed 2.0% by weight so as to avoid negative influence of nic1~el on radiation stcibility of the steel.
Molybdenum content is within the range providing for elimlnation o~ the tempering embrit-tlement, as well as for increasing the hardening depth of steel which is required to obtain high strength and plasticit~.
Vanadium is used as the alement favouring the I`ormation of ~ine-grained structure, bondi~g of nitrogen and improving -tempering stability of steel. The upper limit OL vanadium conte~t of 0.15% by weight is defined by vJelding conlitions.
~ erium is used to improve deformability of the steel in forgin~ and rolling of lar~e-sized ingots. ~he upper li~it of zerium content (0.08% b~ weight) is defined bg the d~.ger of contamination of steel v~ith zerium oxides which may impair deformability and induce the appearance of flaws.
Tho contents of sulphur and phosphorus within the above--mentioned ran~es contribute to additional improvement of toughness of the steel.
The steel having the above composition is manufactured in the form of in~ots weighing up to 160 tons and may be used -'7 ,,, . . ~ ,. . . . . . ................... . . .
.. . .
1~8699~
in forgings and sheets. After hardening and temper, the steel has the following guaranteed mechanical properties with a wall thickness of up to 650 mm:
at 20C - yield strength C-t ~ 55 kg/mm time resistance ~ ~ 62 kg/mm2 percentage elongation ~ ~ 15%
percentage reduction in area ~ ~ 55%
at 350C - ~-t ~ 45 kg/mm2 10or~ ~ 55 kg/mm2 14%
~ ~ 50%
The steel may be welded by automatic, manual or electroslag remelting methods. There is no need in immediate tempering after welding and corrosion resistance surfacing.
Transition embrittlement temperature Tk determined by the work of destruction of V-notched Sharp samples equal to 4.8 kgm i5 not below -40C in the initial state, an increase of Tk after irradiation at 275 to 300C with different fluences is a~ follows:
1.1019 neutr./cm2 S 20 5 1ol9 " " ~ 30 1 1o20 " " ~ 500 ; Upon the above-mentioned changes in the transition temperature, the steel fully complies with the requirements as to resistance against radiation embrittlement imposed by the .
~6g9~
Rules on Strength Calculations of Thick-Walled Containment Structures for Atomic Power Plants adopted in the USSR and abroad. According to these Rules, the use of the steel will ensure safe operation of casings of water-water reactors dur-ing at least 30 years with a fluence of neutrons at the casing wall of at least 1.102 neutr./cm2.
Example 1 me steel having the following composition (in % by weight) was tested: carbon 0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, cerium (from calculation)-O.Ol, sulphur-O.Oll, phosphorus-0.009, copper-0.03, antimony-O.OOl, tin-0.002, iron- the balance. After a heat treatment under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength ~t = 59 1 kgf/mm2 at room temper-ature. Transition embrittlement temperature was Tk= ~90 (with 5x5x27.5 mm samples with 1 mm V-notch.
After irradiation with neutron fluence F=9.7.101 neutr./cm2 (E ~ 0.5 MeV) at 275-320C, the transition temper-ature increased by no more than 10.
Example 2 The steel having the following composition (in % byweight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, cerium (from calculation)-O.Ol, sulphur-O.Oll, phospho-rus-O.OD9, copper-0.06, antimony-O.OOl, tin-0.02, iron-~6g9~
the balance. After a heat treatment under conditions simulat-ing quenching and high temper with the thickness of 650 mm, the steel had yield strength ~t=58.7 kgf/mm2 at room temper-ature. Transition temperature Tk=90C (with 5xSx27.5 mm samples). After irradiation with neutron fluence rate F = 9.7.1019 neutr./cm at 275-320C, the transition temper-ature increased by no more than 10.
Example 3 The steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, sulphur-0.011, phosphorus-0.009, copper-0.08, antimony-0.001, tin-0.002, cerium (from calculation)-0.01, iron-the balance.
After a heat treatment of a sample of this steel under condi-tions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 59.6 kgf/mm2 at room temperature. Transition embrittlement temperature Tk=
-90C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.1019 neutr./cm2 (E
0.5 MeV) at 275-320C, the transition temperature increased by no more than 10C.
Example 4 The steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, man~anese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-~L~8699~
0.12, sulphur~0.011, phosphorus-0.009, copper-0.08, antimony-0.007, tin~0.002, cerium (from calculation-0.01, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating hardening and high temper with the thickness of 650 mm, the steel had yield strength G-t = 59-9 kgf/mm at room temperature (20C). The transition embrittle-ment temperature Tk=-80C (with 5x5x27.5 mm sample~ with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.10 neutr./cm (E ~ 0.5 MeV) at 275-320C the transition temperature increased by 30C.
Example S
~he steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, sulphur-0.011, phosphorus-0.009, copper-0.08, antimony-0.007, tin-0.009, cerium (from calculation)-0.01, iron- the balance. After a heat treatment of samples of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength ~-t =
59.6 kgf/mm2 at room temperature (20C). The transition em-brittlement temperature was Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.10 neutr./cm (E ~ 0.5 MeV) at 275-320C the transi-tion temperature increased by 40C.
Example 6 ~he steel having the following composition (in % by weight) , ~ 8~991~
was tested: carbon - 0.17~ silicon-0.21, ma~ganese~ , c~ro-mium- 1.87, nickel- 1~67, molybdenum- 0.82, vanadium- 0.03, sulphur- 0.013, phosphorus- 0~008~ copper- 0.02, antimony-0~001, tin- 0.001, ~erium ~from calculation)-0.01, iron- the balance. After a heat treatment of a sarnple of this sueel under conditions simulati~g quenching and high ~emper with the th ckness of 650 mm, the steel ~ad yield stren~th 5~r-61.6 kgf/
mm at room temperature (20C). The transition embrittlement temperature ~=-110C (with 5x5x27.5 mm samples with V-notch of 1 rnm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C the transition temperature did not change.
Example 7 The steel having the follovJing com~osition (in % by wei~ht) was tested: carbon- 0.17, silicon-0.21, manganese-O.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.00~, copper-0.02, antimony-0.008, tin-0.002, ~erium (from calculation)-0.01, iron- the balance. After a heat treatment of a sa~ple of this steel under conditions simulating quenching a~d high ternper with the thickness o~ 650 mm, the steel had yield strength ~_ =
62.7 kg/r~m2 at~room tcmperature (20C). The transition ernbrit-tlement temperature ~k=-100C (with 5x5x27.5 mm samples with V-notch o~ 1 mm). A~ter irradiation with neutron fluence rate of 1.2.10~ neutr./cm2 at 285-310C the transition temperature increased by 20C.
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8~
Example 8 The steel having the following composition (in % by weight) was tested, carbon-0.17, silicon-0.21, manganese-0.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.008, copper-0.02, antimony-0.008, tin-0.007, cerium (from calculation)-0.01, iron- the balance.
After a heat treatment of a sample of this steel under condi-tions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 63.1 kgf/mm2 at room temperature. Transition embrittlement temperature Tk=
-90C (with 5xSx27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by 20C.
Example 9 The steel having the following composition (in % by weight) was tested: carbon-0.17, silicon-0.21, manganese-0.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.008, copper-0.10, antimony-0.008, tin-0.007, cerium (from calculation)-0.01, iron- the balance.
After a heat treatment under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength C-t = 63.2 kgf/mm2 at room temperature. Transi-tion embrittlement temperature Tk=-90C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition .
,. ,:
,, ~08~9(~
temperature increased by 30C.
Example 10 The steel having the following composition (in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, sulphur-0.007, phosphorus-0.011, copper-0.06, antimony-0.002, tin-0.0005, cerium (from calculation)-0.02, iron- the balance. A-fter a heat treatment of a sample of this steel un-der conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 58.3 kgf/mm at room temperature. The transition embrittlement temperature Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by no more than 10C.
Example 11 me steel having the following composition (in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel~l.l9, molybdenum-0.70, vanadium-0.06, sulphur-0.007, phosphorus-0.011, copper-0.06, antimony-0.002, tin-0.004, cerium (from calculation)-0.02, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating hardening and high temper with the thickness of 650 mm, the steel had yield strength ~t =
59.3 kgf/mm at room temperature~ The transition embrittle-ment temperature Tk=-80 C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by no more than 10C.
-1~8~i99~
Example 12 The steel having the following composition ~in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, cerium ~from calculation-0.02, sulphur-0.007, phosphorus- ;
0.011, copper-0.06, antimony-0.007, tin-0.004, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield limit ~t =57.9 kgf/mm2 ak room temperature. Ihe transition embrittlement temperature Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.10 neutr./cm2 at 285~310C, the transition temperature increased by 30C.
Example 13 The steel having the following composition (in % by weight) was tested: carbon-0~18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, cerium (from calculation)-0.02, sulphur-0.007, phospho-rus-0.011, copper-0.06, antimony-0.007, tin-0.008, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield limit Gt =58.2 kgf/mm2 at room temperature (20C). The transitioll embrittle-ment temperature Tk=-80C (with Sx5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by 50C.
. . -'. .
101~699~
a quantity of sulphur and phosphorLIs less than or equal to 0~025Yo by weiOht, iron- the balance. ~he steel exhiGit~ high strength (yield strength equal to or less tha~ 55 kg/mm2) and good resistance against radiation (an increase in the transiti~
on embrittlement temperature ~ ~k is less t~an or equal to 60C with a ~eutron fluence of about 1.102 neutr /cm2). ~his steel ca~not, however9 be used for the manufacture of structu-ral members with a wall thickness exceeding 400 mm, and u~elding o~ such members is associated with difficulties because an accompanying heating at 300-350C and immediate temperin~
are required after the welding.
~nown i~ the art is steel consisting o~ 0.25% by weight of carbon, 0~15-0.3% by weight of silicon, 0~5-1~5% by weight of manganese, 0.4-0.7~0 by weight o~ nickel, 0~45-0.6~o by weight of molybdenum, 0.04% by weight of sulphur, 0.035% by weight o~ phosphorus, iron- the balance. ~his steel fea-tures ~ood manufacturing properties and weldability, but is charac-terized b~ low strength (yield strength equal to or less than 35 kg/~2)~ is embri~tled under the action o~ neutron radiati-o~ ( d ~=10~-2~0C with a ~luence o~ neutrons o~ about 5.~lo19 neutr. /cm2).
Also known in the art is s~eel containing 0~20% by weight o~ carbon, 0.020-0.3% by weight of silicon, 0.4% by weight of manganese, 1~5-~.0% by weight o~ chromium, 3-4% by weight of ~ickel, 0.45-0.60% by weight of molybdenum, 0.03% by weight of vanadium, ~ 0.02% by weight of sulphur and phosphorus, iron- the balance.
. .:.. ' . ,~ ' ,,. :: . ';' , ., , ; ,' , . . . . .
. : : . ~ . ,: ., . : . ~ : .
.
... . . . . . . . . . . ..
. . . . .
L08~;99~ ~
~ his steel exhiDi-ts high stre~th (yield stre~gth e~ual to or less than 60 kg~/mm2) and high toughness, it is good ~or welding. Howeverg this s-teel is prone to embrittlement A under heat and radiation action ( ~ Tk=1~-150C with a fluence of neutrons o~ about 5.1019 neutr./cm2).
It is an object o~ the invention to eliminate -the above disadvantages r The main object of the invention i~ to pxovide steel to be used in the manu~acture o~ casin~s of neuclear reactors which exhibits an improved resistance a$ainst the action of neutxon radiation.
Another object of the invention is to provide steel which exhibits an improved hardening depth.
~ he invention consists in the provision of steel conta-ning such components and in such proportions as to improve -~
t~e resistance of steel against the action o~ neutron radiation ;
and increase hardening depth of the steel.
Summary o~ the Invention The above objects are accomplished by that steel contai-ning carbon9 silicon9 manganese, ohromium, nickel, molybdenum, vanadium, ~erium, sulphur, phospho~us and iron, according to the invehtion, additionally contains copper9 antimony and ti~ the above-mentioned component~ being used in the ~ollo-wing quantities, in % by weight:
- . - . " . : . .. ~ .. .. ; : ~ ,: :
; . . . .... .....
, ~
',., , , ' ~ ~ ' ., ;,~
.
:~D86990 carbon 0.12-0.20 silicon 0.15-0.37 manganese 0.3-0.8 chromiu~ 1.6-2.7 nickel 0.8-2.0 molybdenum o.5_~o vanadium 0.05_0.15 ~erium 0.002-0.08 sulphur 0,001-~ 02 phosphorus 0.oo2-o.o2 copper 0.01-0.1 ~ntimony o.ooo5_o,009 tin 0-0005-0.009 iron the balance Accordi~g to the invention, a total content of antimony and tin i~ the steel is preferably from 0~001 to 0.01% by weight.
Due to the present invention it is now possible to provi-de steel exhibiti~g an improved resistance against neutron radiation. At 300C and fluence of neutro~s of 1.102 neutr./cm (~ ~ 0.5 MeV), the transition embrittlemRnt temperature is increased by ~o more than 50C. ~he steel can be u~ed i~
structural members wi~h a wall thickness of up to 650 mm and has an ultimate strength ~ ab 350C of at least 55 kgf/mm2.
The steel does not require immediate tempering a~ter welding.
~urther objects and advantages of the inve~tion will become apparent from the following detailed description of ~, 5 ,: :
.
..
' ~:
, . -, , . . . . ... . .. . . - . ~ . . . . . ~
~, . ., i :
. .. . . . . . .
... . . . . ... . . . . . . .. . . .. . . .. . .
8699~
the steel and pre~erred embodiments o-f the invention.
Detailed Description The steel according to the invention has the following coraposition: 0.12-0.2~)% by weight of carbon, 0.15-0.37% by weight of silicon, 0.3-0.8% by weight of manganese, 1.6-2.7%
by weight of chromium, 0.8-2.0% by weight of nickel, 0.5-1.0~o by wei~ht o~ molybdenum, 0.05-0.15% by wei~ht of vanadium, 0.002-0.08% by weight of ~erium, 0.01-0.10% by weight of copper, 0.0005-0.009~0 by weight of antimony, 0.0005-0 009%
b~ weight of tin, 0.001-0.02% b~ weight of sulphur, 0 002-0.02( % by weight of phosphorus, 96~246-92.862% by weight of iron.
~ he above-mentioned contents of copper, antimony and tin, in combination, impart to the steel according to the invention resistance against radiation-induced embrittlement.
Carbon content in the steel is from 0.12 to 0.20% by ~eight. With a carbon content in the steel at least 0.12% by w~ight, time resistance of at least 62 kgf/mm2 is ensured at 20C. For good welding properties of the steel, carbon content is not to exceed 0.20% by weight.
Silicon and manganese are used in quantities providing for complete desoxidation o~ steel. ~he upper limit of their content is de~ined by the above-mentioned values to prevent lowering of toughness of the steel.
Chromium content of at least 1.6~o by weight provides for requlred strer~th ,rd toughnsss Or the stssl with a wall . .
, ~ ' .
.
. :
.
. .. ,, . ., : .
. . . . . . . . . .
.. '. ' ' , . ' . ... . . . . . , ~ , : . . . . .
. ~ . . .
, .
8~g9 tliickness o~ up to ~5~ mrL. ~ith chromium content no~ e~oeedir,~
2.7~o b,y wei~h-t, ~ood ~eld.3bility of the steel i_ ensured.
Niclcel is used in the steel as the elemen-t which is most favourable for improving hardenin~ depth and toughness of steel. However, nickel content in steel is not to exceed 2.0% by weight so as to avoid negative influence of nic1~el on radiation stcibility of the steel.
Molybdenum content is within the range providing for elimlnation o~ the tempering embrit-tlement, as well as for increasing the hardening depth of steel which is required to obtain high strength and plasticit~.
Vanadium is used as the alement favouring the I`ormation of ~ine-grained structure, bondi~g of nitrogen and improving -tempering stability of steel. The upper limit OL vanadium conte~t of 0.15% by weight is defined by vJelding conlitions.
~ erium is used to improve deformability of the steel in forgin~ and rolling of lar~e-sized ingots. ~he upper li~it of zerium content (0.08% b~ weight) is defined bg the d~.ger of contamination of steel v~ith zerium oxides which may impair deformability and induce the appearance of flaws.
Tho contents of sulphur and phosphorus within the above--mentioned ran~es contribute to additional improvement of toughness of the steel.
The steel having the above composition is manufactured in the form of in~ots weighing up to 160 tons and may be used -'7 ,,, . . ~ ,. . . . . . ................... . . .
.. . .
1~8699~
in forgings and sheets. After hardening and temper, the steel has the following guaranteed mechanical properties with a wall thickness of up to 650 mm:
at 20C - yield strength C-t ~ 55 kg/mm time resistance ~ ~ 62 kg/mm2 percentage elongation ~ ~ 15%
percentage reduction in area ~ ~ 55%
at 350C - ~-t ~ 45 kg/mm2 10or~ ~ 55 kg/mm2 14%
~ ~ 50%
The steel may be welded by automatic, manual or electroslag remelting methods. There is no need in immediate tempering after welding and corrosion resistance surfacing.
Transition embrittlement temperature Tk determined by the work of destruction of V-notched Sharp samples equal to 4.8 kgm i5 not below -40C in the initial state, an increase of Tk after irradiation at 275 to 300C with different fluences is a~ follows:
1.1019 neutr./cm2 S 20 5 1ol9 " " ~ 30 1 1o20 " " ~ 500 ; Upon the above-mentioned changes in the transition temperature, the steel fully complies with the requirements as to resistance against radiation embrittlement imposed by the .
~6g9~
Rules on Strength Calculations of Thick-Walled Containment Structures for Atomic Power Plants adopted in the USSR and abroad. According to these Rules, the use of the steel will ensure safe operation of casings of water-water reactors dur-ing at least 30 years with a fluence of neutrons at the casing wall of at least 1.102 neutr./cm2.
Example 1 me steel having the following composition (in % by weight) was tested: carbon 0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, cerium (from calculation)-O.Ol, sulphur-O.Oll, phosphorus-0.009, copper-0.03, antimony-O.OOl, tin-0.002, iron- the balance. After a heat treatment under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength ~t = 59 1 kgf/mm2 at room temper-ature. Transition embrittlement temperature was Tk= ~90 (with 5x5x27.5 mm samples with 1 mm V-notch.
After irradiation with neutron fluence F=9.7.101 neutr./cm2 (E ~ 0.5 MeV) at 275-320C, the transition temper-ature increased by no more than 10.
Example 2 The steel having the following composition (in % byweight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, cerium (from calculation)-O.Ol, sulphur-O.Oll, phospho-rus-O.OD9, copper-0.06, antimony-O.OOl, tin-0.02, iron-~6g9~
the balance. After a heat treatment under conditions simulat-ing quenching and high temper with the thickness of 650 mm, the steel had yield strength ~t=58.7 kgf/mm2 at room temper-ature. Transition temperature Tk=90C (with 5xSx27.5 mm samples). After irradiation with neutron fluence rate F = 9.7.1019 neutr./cm at 275-320C, the transition temper-ature increased by no more than 10.
Example 3 The steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, sulphur-0.011, phosphorus-0.009, copper-0.08, antimony-0.001, tin-0.002, cerium (from calculation)-0.01, iron-the balance.
After a heat treatment of a sample of this steel under condi-tions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 59.6 kgf/mm2 at room temperature. Transition embrittlement temperature Tk=
-90C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.1019 neutr./cm2 (E
0.5 MeV) at 275-320C, the transition temperature increased by no more than 10C.
Example 4 The steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, man~anese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-~L~8699~
0.12, sulphur~0.011, phosphorus-0.009, copper-0.08, antimony-0.007, tin~0.002, cerium (from calculation-0.01, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating hardening and high temper with the thickness of 650 mm, the steel had yield strength G-t = 59-9 kgf/mm at room temperature (20C). The transition embrittle-ment temperature Tk=-80C (with 5x5x27.5 mm sample~ with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.10 neutr./cm (E ~ 0.5 MeV) at 275-320C the transition temperature increased by 30C.
Example S
~he steel having the following composition (in % by weight) was tested: carbon-0.12, silicon-0.27, manganese-0.48, chromium-2.47, nickel-1.14, molybdenum-0.56, vanadium-0.12, sulphur-0.011, phosphorus-0.009, copper-0.08, antimony-0.007, tin-0.009, cerium (from calculation)-0.01, iron- the balance. After a heat treatment of samples of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength ~-t =
59.6 kgf/mm2 at room temperature (20C). The transition em-brittlement temperature was Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 9.7.10 neutr./cm (E ~ 0.5 MeV) at 275-320C the transi-tion temperature increased by 40C.
Example 6 ~he steel having the following composition (in % by weight) , ~ 8~991~
was tested: carbon - 0.17~ silicon-0.21, ma~ganese~ , c~ro-mium- 1.87, nickel- 1~67, molybdenum- 0.82, vanadium- 0.03, sulphur- 0.013, phosphorus- 0~008~ copper- 0.02, antimony-0~001, tin- 0.001, ~erium ~from calculation)-0.01, iron- the balance. After a heat treatment of a sarnple of this sueel under conditions simulati~g quenching and high ~emper with the th ckness of 650 mm, the steel ~ad yield stren~th 5~r-61.6 kgf/
mm at room temperature (20C). The transition embrittlement temperature ~=-110C (with 5x5x27.5 mm samples with V-notch of 1 rnm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C the transition temperature did not change.
Example 7 The steel having the follovJing com~osition (in % by wei~ht) was tested: carbon- 0.17, silicon-0.21, manganese-O.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.00~, copper-0.02, antimony-0.008, tin-0.002, ~erium (from calculation)-0.01, iron- the balance. After a heat treatment of a sa~ple of this steel under conditions simulating quenching a~d high ternper with the thickness o~ 650 mm, the steel had yield strength ~_ =
62.7 kg/r~m2 at~room tcmperature (20C). The transition ernbrit-tlement temperature ~k=-100C (with 5x5x27.5 mm samples with V-notch o~ 1 mm). A~ter irradiation with neutron fluence rate of 1.2.10~ neutr./cm2 at 285-310C the transition temperature increased by 20C.
~ .
.
.
. ~. ` ' ` ' ' ; ' . .
8~
Example 8 The steel having the following composition (in % by weight) was tested, carbon-0.17, silicon-0.21, manganese-0.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.008, copper-0.02, antimony-0.008, tin-0.007, cerium (from calculation)-0.01, iron- the balance.
After a heat treatment of a sample of this steel under condi-tions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 63.1 kgf/mm2 at room temperature. Transition embrittlement temperature Tk=
-90C (with 5xSx27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by 20C.
Example 9 The steel having the following composition (in % by weight) was tested: carbon-0.17, silicon-0.21, manganese-0.34, chromium-1.87, nickel-1.67, molybdenum-0.82, vanadium-0.08, sulphur-0.013, phosphorus-0.008, copper-0.10, antimony-0.008, tin-0.007, cerium (from calculation)-0.01, iron- the balance.
After a heat treatment under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength C-t = 63.2 kgf/mm2 at room temperature. Transi-tion embrittlement temperature Tk=-90C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition .
,. ,:
,, ~08~9(~
temperature increased by 30C.
Example 10 The steel having the following composition (in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, sulphur-0.007, phosphorus-0.011, copper-0.06, antimony-0.002, tin-0.0005, cerium (from calculation)-0.02, iron- the balance. A-fter a heat treatment of a sample of this steel un-der conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield strength G-t = 58.3 kgf/mm at room temperature. The transition embrittlement temperature Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by no more than 10C.
Example 11 me steel having the following composition (in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel~l.l9, molybdenum-0.70, vanadium-0.06, sulphur-0.007, phosphorus-0.011, copper-0.06, antimony-0.002, tin-0.004, cerium (from calculation)-0.02, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating hardening and high temper with the thickness of 650 mm, the steel had yield strength ~t =
59.3 kgf/mm at room temperature~ The transition embrittle-ment temperature Tk=-80 C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by no more than 10C.
-1~8~i99~
Example 12 The steel having the following composition ~in % by weight) was tested: carbon-0.18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, cerium ~from calculation-0.02, sulphur-0.007, phosphorus- ;
0.011, copper-0.06, antimony-0.007, tin-0.004, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield limit ~t =57.9 kgf/mm2 ak room temperature. Ihe transition embrittlement temperature Tk=-80C (with 5x5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.10 neutr./cm2 at 285~310C, the transition temperature increased by 30C.
Example 13 The steel having the following composition (in % by weight) was tested: carbon-0~18, silicon-0.32, manganese-0.55, chromium-2.31, nickel-l.l9, molybdenum-0.70, vanadium-0.06, cerium (from calculation)-0.02, sulphur-0.007, phospho-rus-0.011, copper-0.06, antimony-0.007, tin-0.008, iron- the balance. After a heat treatment of a sample of this steel under conditions simulating quenching and high temper with the thickness of 650 mm, the steel had yield limit Gt =58.2 kgf/mm2 at room temperature (20C). The transitioll embrittle-ment temperature Tk=-80C (with Sx5x27.5 mm samples with V-notch of 1 mm). After irradiation with neutron fluence of 1.2.102 neutr./cm2 at 285-310C, the transition temperature increased by 50C.
. . -'. .
Claims (2)
1. Steel consisting of the following components, in %
by weight:
Carbon 0.12-0.20 silicon 0.15-0.37 manganese 0.3-0.8 chromium 1.6-2.7 nickel 0.8-2.0 molybdenum 0.5-1.0 vanadium 0.05-0.15 cerium 0.002-0.08 copper 0.01-0.10 antimony 0.0005-0.009 tin 0.0005-0.009 sulphur 0.001-0.02 phosphorus 0.002-0.02 iron 96.246-92.862.
by weight:
Carbon 0.12-0.20 silicon 0.15-0.37 manganese 0.3-0.8 chromium 1.6-2.7 nickel 0.8-2.0 molybdenum 0.5-1.0 vanadium 0.05-0.15 cerium 0.002-0.08 copper 0.01-0.10 antimony 0.0005-0.009 tin 0.0005-0.009 sulphur 0.001-0.02 phosphorus 0.002-0.02 iron 96.246-92.862.
2. Steel according to Claim 1, wherein the total content of antimony and tin is from 0.001 to 0.01% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA000290035A CA1086990A (en) | 1977-11-01 | 1977-11-01 | Low alloy steel for nuclear applications |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA000290035A CA1086990A (en) | 1977-11-01 | 1977-11-01 | Low alloy steel for nuclear applications |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1086990A true CA1086990A (en) | 1980-10-07 |
Family
ID=4109920
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000290035A Expired CA1086990A (en) | 1977-11-01 | 1977-11-01 | Low alloy steel for nuclear applications |
Country Status (1)
| Country | Link |
|---|---|
| CA (1) | CA1086990A (en) |
-
1977
- 1977-11-01 CA CA000290035A patent/CA1086990A/en not_active Expired
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