CN102409258A - Boron-containing high strength hydrogen embrittlement resistant alloy and structural homogeneity control method thereof - Google Patents

Boron-containing high strength hydrogen embrittlement resistant alloy and structural homogeneity control method thereof Download PDF

Info

Publication number
CN102409258A
CN102409258A CN2011103464945A CN201110346494A CN102409258A CN 102409258 A CN102409258 A CN 102409258A CN 2011103464945 A CN2011103464945 A CN 2011103464945A CN 201110346494 A CN201110346494 A CN 201110346494A CN 102409258 A CN102409258 A CN 102409258A
Authority
CN
China
Prior art keywords
alloy
hydrogen embrittlement
boracic
boron
hydrogen
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.)
Granted
Application number
CN2011103464945A
Other languages
Chinese (zh)
Other versions
CN102409258B (en
Inventor
赵明久
戎利建
闫德胜
姜海昌
刘树伟
胡晓峰
王本贤
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Institute of Metal Research of CAS
Original Assignee
Institute of Metal Research of CAS
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Institute of Metal Research of CAS filed Critical Institute of Metal Research of CAS
Priority to CN2011103464945A priority Critical patent/CN102409258B/en
Publication of CN102409258A publication Critical patent/CN102409258A/en
Application granted granted Critical
Publication of CN102409258B publication Critical patent/CN102409258B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • YGENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02PCLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00Technologies related to metal processing
    • Y02P10/20Recycling

Abstract

The invention relates to the field of precipitate strengthened Fe-Ni based austenite alloys, in particular to a boron-containing high strength hydrogen embrittlement resistant alloy and a structural homogeneity control method thereof. The alloy comprises the following components by weight percent: 0.001-0.01% of B, 29.5-31.5% of Ni, 13.5-16.5% of Cr, 1.1-1.5% of Mo, 0.1-0.5% of V, 1.6-2.4% of Ti, 0.1-0.6% of Al and the balance of Fe and inevitable residual elements. The alloy and the method have the following advantages and beneficial effects: when the boron content is 0.001-0.004%, the solution treatment method in which the temperature is 970-990 DEG C and water quenching is carried out after the heat is preserved for 0.5-2 hours is adopted, and when the boron content is 0.004-0.01%, the solution treatment method in which the temperature is 1020-1040 DEG C and water quenching is carried out after the heat is preserved for 0.5-2 hours is adopted, thus eliminating local fine grain structures in the alloy; and precipitation of the grain boundary harmful eta phase can be restrained, the room-temperature ductility of the alloy is improved, and the yield strength of the alloy is ensured to be 690-750MPa, the tensile strength is ensured to be 980-1000MPa, the elongation is ensured to be 24-30%, the reduction of area is ensured to be 35-45% and the hydrogen-induced ductility is ensured to be reduced to 30-45% after the alloy is put in the high purity hydrogen environment at a temperature of 300 DEG C and a pressure of 10MPa for 10 days.

Description

A kind of HS of boracic, the alloy of anti-hydrogen embrittlement the and homogeneity of structure control method thereof
Technical field
The present invention relates to precipitation strength Fe-Ni based austenite alloy field, specifically a kind of HS of boracic, the alloy of anti-hydrogen embrittlement the and homogeneity of structure control method thereof.
Background technology
Precipitation strength Fe-Ni based austenite alloy grows up on single-phase austenitic alloy basis, and the high-intensity source of such alloy is in having strengthening phase γ '-Ni that coherence concerns with matrix 3(Al, Ti), typical alloy such as external A286, JBK-75, domestic J75, J90 also belong to this type of alloy.Add boron at precipitation strength Fe-Ni based austenite alloy (like the J75 alloy), can effectively suppress alloy and in ag(e)ing process, separate out crystal boundary η-Ni 3The Ti phase is improved alloy at room temperature plasticity and hydrogen embrittlement resistance ability.Discover that with the increase of boron content in the alloy, the recrystallization temperature of alloy and grain growth speed can change, be easy in alloy, occur local thin Jingjing tissue (like Fig. 1), worsen alloy at room temperature mechanical property and anti-hydrogen embrittlement ability.Precipitation strength Fe-Ni based austenite alloy is under the state of solid solution+ageing treatment, to use, and therefore through suitable solid solution treatment method, eliminates local fine grained texture, realizes the control of alloy structure homogeneity, and is significant for the practical applications of this kind alloy.
Summary of the invention
The object of the present invention is to provide a kind of HS of boracic, the alloy of anti-hydrogen embrittlement the and homogeneity of structure control method thereof; Boron content does not have different hydrogen embrittlement resistance abilities simultaneously in this kind alloy; The homogeneity of structure control method that provides simultaneously can be eliminated because boron content increases the local fine grained texture that is brought, and realizes the control of alloy structure homogeneity.
Technical scheme of the present invention is:
A kind of HS of boracic, the alloy of anti-the hydrogen embrittlement, its staple scope is (weight percent) as follows:
Ni:29.5~31.5, Cr:13.5~16.5, Mo:1.1~1.5, vanadium: 0.1~0.5, titanium: 1.6~2.4, aluminium: 0.1~0.6, boron: 0.001~0.01, iron and inevitable residual element: surplus.
The HS of described boracic, the alloy of anti-the hydrogen embrittlement, inevitably residual element comprise: carbon, sulphur, phosphorus, by weight percentage, carbon content is controlled at≤0.015, and sulphur content is controlled at≤0.00, and phosphorus content is controlled at≤and 0.006.
The HS of above-mentioned boracic, anti-hydrogen embrittlement alloy organizing homogeneity control method adopt vacuum induction melting → steel die cast → ingot homogenization → forged method to prepare alloy bar material, reach the reinforcement of alloy again through solid solution+ageing treatment.Through adopting the CaO crucible to carry out vacuum induction melting, effectively control carbon, sulphur, phosphorus impurities content in the alloy, the hydrogen embrittlement resistance that improves alloy can; Bar through forging, the required specification of rolling acquisition; Through final solid solution+timeliness thermal treatment, eliminate local fine grained texture and make the γ ' strengthening phase of separating out suitable size and quantity in the alloy, guarantee that alloy has high intensity and plasticity coupling, concrete steps are following:
1, is raw material with technically pure iron, electrolytic nickel, chromium metal, metal molybdenum and other master alloy (as: ferro-boron, vanadium iron, ferrotianium and ferro-aluminum), adopts the CaO crucible to carry out vacuum induction melting, the cast ingot casting.The chemical ingredients (weight percent) of control in the alloy be as follows:
Ni:29.5~31.5, Cr:13.5~16.5, Mo:1.1~1.5, vanadium: 0.1~0.5, titanium: 1.6~2.4, aluminium: 0.1~0.6, boron: 0.001~0.01, carbon≤0.015, sulphur≤0.005, phosphorus≤0.006, iron: surplus.
2, said ingot casting carries out 1160~1200 ℃ homogenizing processing, when boron content is lower than 0.004, and soaking time 22~26h; When boron content during in 0.004~0.01 scope, soaking time 46~50h.
3, after the said homogenizing cast ingot, behind 1050~1150 ℃ of insulation 2~8h, carry out alloy forging, 1050~1150 ℃ of cogging forging temperatures, 900~1000 ℃ of final forging temperatures obtain to forge rod; Allow to melt down reheat forging to final specification, at 1050~1150 ℃ of insulation 1~3h down.
4, said forging rod is rolled behind 1050~1150 ℃ of insulation 2~4h, 1050~1150 ℃ of split rolling method temperature, and 900~1000 ℃ of finishing temperatures should once be rolled into required scale rod bar, do not carry out process annealing and handle.
5, the rod of getting in the step 4 that rolls carries out solution treatment, and when boron content was lower than 0.004, solid solution temperature was controlled at 970~990 ℃, soaking time 0.5~2h, shrend; When boron content during in 0.004~0.01 scope, solid solution temperature is controlled at 1020~1040 ℃, soaking time 0.5~2h, shrend.
6, get the ageing treatment that the bar after solution treatment in the step 5 carries out 720~750 ℃ of insulation 8~32h.
7, get the bar after ageing treatment in the step 6, along rolling bar cross metallographic specimen, prepare sample by the microscopic test method of standard, etching reagent is selected the chromic acid of 5~15wt% for use, the tissues observed homogeneity.
8, get the bar after ageing treatment in the step 6, the processing tension specimen carries out mechanical property by GB228-2002 " metal tensile test method " and detects.
9, get in the step 6 processing of the bar after ageing treatment tension specimen, carry out 300 ℃, 10MPa, High Purity Hydrogen (bulk purity >=99.999%), 10 days the hydrogen that fills subsequently and handle, carry out the mechanical property detection by GB228-2002 " metal tensile test method ".
Advantage of the present invention and beneficial effect are:
1, the present invention adopts different homogenizing treatment time and solid solution temperature; Eliminate because boron content increases the component segregation that is brought; And the influence of alloy recrystallization temperature that causes thus and the involutory Jin Jing's particle size of grain growth rate variations; Can in guaranteeing alloy in the abundant solid solutions of element such as Ti, Al, eliminate local fine grained texture, guarantee the stability of alloy structure performance.
2, the ys (σ of alloy of the present invention 0.2) 690~800MPa, tensile strength 980~1100MPa, unit elongation 25~30%, relative reduction in area 50~65%.
3, the alloy among the present invention contains 0.001~0.01% boron, can suppress separating out of the harmful η phase of crystal boundary, improves the alloy temperature-room type plasticity, guarantee that alloy is placed 10 days in 300 ℃, 10MPa High Purity Hydrogen environment after, ys (σ 0.2) be higher than 690~750MPa, tensile strength is higher than 980~1000MPa, unit elongation is higher than 24~30%, relative reduction in area is higher than 35~45%, hydrogen causes plasticity and decreases and to lower in 30~45%.
Description of drawings
Fig. 1 is the alloy microtexture after 980 ℃/1h, shrend+740 ℃/8h, air cooling are handled, and boron is 0.01% (weight percent) in the alloy.
Fig. 2 is the alloy microtexture after 980 ℃/1h, shrend+740 ℃/8h, air cooling are handled, boracic 0.0021% (weight percent) in the alloy.
Fig. 3 is the alloy microtexture after 1030 ℃/1h, shrend+740 ℃/8h, air cooling are handled, boracic 0.0060% (weight percent) in the alloy.
Fig. 4 is the alloy microtexture after 1040 ℃/1h, shrend+740 ℃/8h, air cooling are handled, boracic 0.010% (weight percent) in the alloy.
Embodiment
Embodiment 1: contain the HS of 0.0021wt% boron, the alloy bar material of anti-hydrogen embrittlement the (φ 15mm)
Adopt the CaO crucible, molten alloy on the 25kg vacuum induction furnace, through ingot homogenization, forging, the rolling alloy bar material that is prepared into φ 15mm specification, its chemical ingredients is seen table 1, the preparation process is:
1, be raw material with technically pure iron, electrolytic nickel, chromium metal, metal molybdenum and other master alloy (ferro-boron, vanadium iron, ferrotianium and ferro-aluminum), adopt the CaO crucible to carry out vacuum induction melting, the cast ingot casting, the ingot casting specification is φ 120 * 220mm.
2, said ingot casting carries out the homogenizing processing of 1160~1200 ℃ of insulation 22~26h (present embodiment is 1180 ℃ of insulation 24h).
3, after the said homogenizing cast ingot; Behind 1050~1150 ℃ of insulation 2~8h (present embodiment is that 1140 ℃ of soaking times are 4h), carry out alloy forging; 1050~1150 ℃ of cogging forging temperatures (present embodiment is 1120 ℃); 900~1000 ℃ of final forging temperatures (the present embodiment final forging temperature is 950 ℃) allow to melt down reheat forging to final specification, but the reheat temperature are no less than 1~3h.(present embodiment melts down heating once, is 1.5h 1120 ℃ of soaking times) forged rod and is of a size of φ 30mm.
4, said forging rod is rolled behind 1050~1150 ℃ of insulation 2~4h (present embodiment is that 1120 ℃ of soaking times are 3h); 1050~1150 ℃ of split rolling method temperature (present embodiment is 1100 ℃); 900~1000 ℃ of finishing temperatures (the present embodiment final forging temperature is 920 ℃); Once be rolled into required scale rod bar, do not carry out process annealing and handle, roll rod and be of a size of φ 15mm.
5, the rod of getting in the step 4 that rolls carries out solution treatment, and solid solution temperature is controlled at 970~990 ℃ (present embodiment is 980 ℃), soaking time 0.5~2h (present embodiment is 1h) back shrend.
6, get the ageing treatment that the bar after solution treatment in the step 5 carries out 720~750 ℃ (present embodiment is 740 ℃) insulation 8~32h (present embodiment is 8h).
7, get the bar after ageing treatment in the step 6, along rolling bar cross metallographic specimen, prepare sample by the microscopic test method of standard, etching reagent is selected the chromic acid of 10wt% for use, and the alloy microtexture is seen Fig. 2.This alloy organizing is even, does not have local fine grained texture and occurs.
8, get the processing of the bar after ageing treatment tension specimen in the step 6, carry out mechanical property by GB228-2002 " metal tensile test method " and detect, detected result is seen table 2.
9, get the processing of the bar after ageing treatment tension specimen in the step 6; Carrying out 300 ℃, 10MPa, High Purity Hydrogen (bulk purity 99.999%), 10 days the hydrogen that fills subsequently handles; Carry out mechanical property by GB228-2002 " metal tensile test method " and detect, detected result is seen table 2.
The chemical ingredients of table 1 alloy, massfraction, %
Element B C ?S P Ni Cr
Roll rod 0.0021 0.0034 ?<0.001 0.004 30.2 15.19
Element Ti Al ?Mo V Fe
Roll rod 2.06 0.24 ?1.29 0.27 Surplus
Table 2 alloy room-temperature mechanical property
Annotate: ψ LRepresent alloy hydrogen to cause plasticity and decrease and to subtract, its value is (do not fill hydrogen sample reduction of area value-fill hydrogen sample reduction of area value)/do not fill hydrogen sample reduction of area value, is calculated by three sample means.
Experimental result shows that prepared specification is the alloy bar material that contains 0.0021% boron of φ 15mm, after 980 ℃/1h, shrend+740 ℃/8h, air cooling are handled, does not have local fine grained texture and its ys (σ occurs 0.2) be higher than 740MPa, tensile strength is higher than 1040MPa, unit elongation is higher than 28%, relative reduction in area is higher than 62%; After in 300 ℃, the High Purity Hydrogen environment of 10MPa, placing 10 days, tensile strength is higher than that 1060MPa, ys are higher than 720MPa, unit elongation is higher than 24.5%, and relative reduction in area is higher than 35%, and hydrogen causes plasticity and decreases and lower in 45%.
Embodiment 2: contain the HS of 0.0060wt% boron, the alloy bar material of anti-hydrogen embrittlement the (φ 14mm)
Be that with embodiment 1 difference boracic is 0.0060wt% in the prepared alloy, the bar specification is φ 14mm.
Adopting the CaO crucible, be the raw material molten alloy with technically pure iron, electrolytic nickel, chromium metal, metal molybdenum and other master alloy (ferro-boron, vanadium iron, ferrotianium and ferro-aluminum) on the 25kg vacuum induction furnace, and pouring into a mould the ingot casting specification is φ 120 * 220mm, and alloying constituent is seen table 3.Ingot casting forges 1120 ℃ of cogging forging temperatures after carrying out the homogenizing processing of 1180 ℃ of insulation 48h behind 1140 ℃ of soaking time 5h; 950 ℃ of final forging temperatures; Return heating once forging to the final specification,, forge excellent size φ 30mm at 1120 ℃ of soaking time 1.5h.Forge rod and behind 1120 ℃ of soaking time 3h, be rolled, 1120 ℃ of split rolling method temperature, 920 ℃ of finishing temperatures once are rolled into φ 14mm bar, do not carry out process annealing and handle.Roll rod and carry out shrend solution treatment behind 1030 ℃, insulation 1h, carry out the ageing treatment of air cooling behind 740 ℃ of insulation 8h subsequently.Bar after the ageing treatment can be tested by carrying out microtexture, mechanical property and hydrogen embrittlement resistance with embodiment 1 same procedure, and the result sees Fig. 3 and table 4.
The chemical ingredients of table 3 alloy, massfraction, %
Element B C S P Ni Cr
Roll rod 0.0060 0.0023 <0.0005 0.004 30.1 14.91
Element Ti Al Mo V Fe
Roll rod 1.97 0.19 1.34 0.25 Surplus
Table 4 alloy room-temperature mechanical property
Annotate: ψ LRepresent alloy hydrogen to cause plasticity and decrease and to subtract, its value is (do not fill hydrogen sample reduction of area value-fill hydrogen sample reduction of area value)/do not fill hydrogen sample reduction of area value, is calculated by three sample means.
Experimental result shows that this alloy organizing is even, does not have local fine grained texture and occurs.Prepared specification is the alloy bar material that contains 0.0060% boron of φ 14mm, after 1030 ℃/1h, shrend+740 ℃/8h, air cooling are handled, does not have local fine grained texture and its ys (σ occurs 0.2) be higher than 710MPa, tensile strength is higher than 1030MPa, unit elongation is higher than 27%, relative reduction in area is higher than 60%; After in 300 ℃, the High Purity Hydrogen environment of 10MPa, placing 10 days, tensile strength is higher than that 1030MPa, ys are higher than 740MPa, unit elongation is higher than 23.5%, and relative reduction in area is higher than 40%, and hydrogen causes plasticity and decreases and lower in 33%.
Embodiment 3: contain the HS of 0.010wt% boron, the alloy bar material of anti-hydrogen embrittlement the (φ 15mm)
Be that with embodiment 1 difference boracic is 0.010% in the prepared alloy.
Adopting the CaO crucible, be the raw material molten alloy with technically pure iron, electrolytic nickel, chromium metal, metal molybdenum and other master alloy (ferro-boron, vanadium iron, ferrotianium and ferro-aluminum) on the 25kg vacuum induction furnace, and pouring into a mould the ingot casting specification is φ 120 * 220mm, and alloying constituent is seen table 5.After the homogenizing that ingot casting carries out 1180 ℃ of insulation 48h is handled, behind 1140 ℃ of insulation 5h, forge, 1120 ℃ of cogging forging temperatures, 950 ℃ of final forging temperatures are melted down heating once forging to final specification, and soaking time 2h forges rod and is of a size of φ 30mm.Forge rod and behind 1120 ℃ of soaking time 3h, be rolled, 1120 ℃ of split rolling method temperature, 920 ℃ of finishing temperatures once are rolled into the φ 15mm of institute bar, do not carry out process annealing and handle.Roll rod and carry out the solution treatment of shrend behind 1040 ℃, insulation 1h, carry out the ageing treatment of air cooling behind 740 ℃ of insulation 8h subsequently.Bar after the ageing treatment can be tested by carrying out microtexture, mechanical property and hydrogen embrittlement resistance with embodiment 1 same procedure, and the result sees Fig. 4 and table 6.
The chemical ingredients of table 5 alloy, massfraction, %
Element B C S P Ni Cr
Roll rod 0.010 0.0031 0.0006 0.005 30.0 14.77
Element Ti Al Mo V Fe
Roll rod 1.99 0.19 1.34 0.25 Surplus
Table 6 alloy room-temperature mechanical property
Annotate: ψ LRepresent alloy hydrogen to cause plasticity and decrease and to subtract, its value is (do not fill hydrogen sample reduction of area value-fill hydrogen sample reduction of area value)/do not fill hydrogen sample reduction of area value, is calculated by three sample means.
Experimental result shows that this alloy organizing is even, does not have local fine grained texture and occurs.Prepared specification is the alloy bar material that contains 0.010% boron of φ 15mm, and through 1040 ℃/1h, shrend+740 ℃/8h after air cooling is handled, do not have local fine grained texture and its ys (σ occurs 0.2) be higher than 740MPa, tensile strength is higher than 1065MPa, unit elongation is higher than 25%, relative reduction in area is higher than 53%; After in 300 ℃, the High Purity Hydrogen environment of 10MPa, placing 10 days, tensile strength is higher than that 1030MPa, ys are higher than 730MPa, unit elongation is higher than 23.5%, and relative reduction in area is higher than 35%, and hydrogen causes plasticity and decreases and lower in 32%.

Claims (10)

1. HS, the alloy of anti-hydrogen embrittlement of a boracic is characterized in that, percentage meter by weight, and the scope of this alloy staple is following:
Ni:29.5~31.5, Cr:13.5~16.5, Mo:1.1~1.5, vanadium: 0.1~0.5, titanium: 1.6~2.4, aluminium: 0.1~0.6, boron: 0.001~0.01, iron and inevitable residual element: surplus.
2. according to HS, the alloy of anti-hydrogen embrittlement of the said boracic of claim 1, it is characterized in that inevitably residual element comprise: carbon, sulphur, phosphorus; Percentage meter by weight, in this alloy, carbon content is controlled at≤and 0.015; Sulphur content is controlled at≤and 0.005, phosphorus content is controlled at≤and 0.006.
3. according to HS, the alloy of anti-hydrogen embrittlement of the said boracic of claim 1, it is characterized in that the ys 690~800MPa of alloy, tensile strength 980~1100MPa, unit elongation 25~30%, relative reduction in area 50~65%.
4. according to HS, the alloy of anti-hydrogen embrittlement of the said boracic of claim 1; It is characterized in that; Alloy is placed after 10 days in 300 ℃, 10MPa High Purity Hydrogen environment, and ys is higher than 690~750MPa, tensile strength is higher than 980~1000MPa, and unit elongation is higher than 24~30%; Relative reduction in area is higher than 35~45%, and hydrogen causes the plasticity damage and lowers in 30~45%.
5. the HS of the said boracic of one of claim 1~4, anti-hydrogen embrittlement alloy organizing homogeneity control method is characterized in that it is following that alloy prepares detailed process:
(1) adopt the CaO crucible to carry out the vacuum induction melting alloy, the cast ingot casting;
(2) 1160~1200 ℃ of homogenizing of ingot casting are handled;
(3) alloy forging;
(4) alloy rolling;
(5) bar thermal treatment.
6. by HS, the anti-hydrogen embrittlement alloy organizing homogeneity control method of the said boracic of claim 5, it is characterized in that: in the said step (2), when boron content is lower than 0.004, soaking time 22~26h; When boron content during in 0.004~0.01 scope, soaking time 46~50h.
7. press HS, the anti-hydrogen embrittlement alloy organizing homogeneity control method of the said boracic of claim 5; It is characterized in that: in the said step (3); Behind 1050~1150 ℃ of insulation 2~8h, carry out alloy forging, 1050~1150 ℃ of cogging forging temperatures, 900~1000 ℃ of final forging temperatures.
8. by HS, the anti-hydrogen embrittlement alloy organizing homogeneity control method of the said boracic of claim 7, it is characterized in that: in the said step (3), before being swaged into final specification, allowing to melt down reheat, is 1~3h 1050~1150 ℃ of soaking times.
9. press HS, the anti-hydrogen embrittlement alloy organizing homogeneity control method of the said boracic of claim 5; It is characterized in that: in the said step (4); Behind 1050~1150 ℃ of insulation 2~4h, be rolled 1050~1150 ℃ of split rolling method temperature, 900~1000 ℃ of finishing temperatures; Once be rolled into required scale rod bar, do not carry out process annealing and handle.
10. press HS, the anti-hydrogen embrittlement alloy organizing homogeneity control method of the said boracic of claim 5; It is characterized in that: in the said step (5), when boron content was lower than 0.004, solid solution temperature was controlled at 970~990 ℃; Soaking time 0.5~2h, shrend; When boron content during in 0.004~0.01% scope, solid solution temperature is controlled at 1020~1040 ℃, soaking time time 0.5~2h, shrend; Bar after solution treatment carries out 720~750 ℃ of ageing treatment that are incubated 8~32h.
CN2011103464945A 2011-11-04 2011-11-04 Structural homogeneity control method of boron-containing high strength hydrogen resistant brittle alloy Active CN102409258B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN2011103464945A CN102409258B (en) 2011-11-04 2011-11-04 Structural homogeneity control method of boron-containing high strength hydrogen resistant brittle alloy

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN2011103464945A CN102409258B (en) 2011-11-04 2011-11-04 Structural homogeneity control method of boron-containing high strength hydrogen resistant brittle alloy

Publications (2)

Publication Number Publication Date
CN102409258A true CN102409258A (en) 2012-04-11
CN102409258B CN102409258B (en) 2013-07-10

Family

ID=45911595

Family Applications (1)

Application Number Title Priority Date Filing Date
CN2011103464945A Active CN102409258B (en) 2011-11-04 2011-11-04 Structural homogeneity control method of boron-containing high strength hydrogen resistant brittle alloy

Country Status (1)

Country Link
CN (1) CN102409258B (en)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102699636A (en) * 2012-06-18 2012-10-03 西南大学 Liquid die-forging and rolling composite forming method for 6082 aluminum alloy special-section large ring piece
CN102719642A (en) * 2012-06-21 2012-10-10 中国科学院金属研究所 Production process of high-strength high-toughness GH2132 rod/wire material
CN102994908A (en) * 2012-11-21 2013-03-27 中国科学院金属研究所 Control method of ultra-low-carbon, high strength, hydrogen embrittlement-resistant alloy and non-metallic inclusion of austenitic alloy
CN105063507A (en) * 2015-08-20 2015-11-18 中国科学院金属研究所 High-strength hydrogen-brittleness-resistant austenite alloy with mark of J75 and preparation method of high-strength hydrogen-brittleness-resistant austenite alloy

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1282381A (en) * 1997-12-19 2001-01-31 埃克森美孚上游研究公司 Ultra-high strength steels with excellent cryogenic temp. toughness
CN102066594A (en) * 2008-06-16 2011-05-18 住友金属工业株式会社 Heat-resistant austenitic alloy, heat-resistant pressure-resistant member comprising the alloy, and process for producing the same

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1282381A (en) * 1997-12-19 2001-01-31 埃克森美孚上游研究公司 Ultra-high strength steels with excellent cryogenic temp. toughness
CN102066594A (en) * 2008-06-16 2011-05-18 住友金属工业株式会社 Heat-resistant austenitic alloy, heat-resistant pressure-resistant member comprising the alloy, and process for producing the same

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
《材料研究学报》 20060430 李秀艳 等 Fe_Ni基合金中次生eta相的析出机理 113-119 1-10 第20卷, 第2期 *
张建 等: "晶界相对Fe_Ni_Cr奥氏体合金氢脆的影响", 《金属学报》 *
李秀艳 等: "Fe_Ni基合金中次生η相的析出机理", 《材料研究学报》 *
赵明久 等: "B对Fe_Ni基合金显微组织和抗氢性能的影响", 《金属学报》 *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102699636A (en) * 2012-06-18 2012-10-03 西南大学 Liquid die-forging and rolling composite forming method for 6082 aluminum alloy special-section large ring piece
CN102699636B (en) * 2012-06-18 2015-08-19 西南大学 The liquid forging Rolling compund manufacturing process of 6082 aluminium alloy different cross section large rings
CN102719642A (en) * 2012-06-21 2012-10-10 中国科学院金属研究所 Production process of high-strength high-toughness GH2132 rod/wire material
CN102994908A (en) * 2012-11-21 2013-03-27 中国科学院金属研究所 Control method of ultra-low-carbon, high strength, hydrogen embrittlement-resistant alloy and non-metallic inclusion of austenitic alloy
CN105063507A (en) * 2015-08-20 2015-11-18 中国科学院金属研究所 High-strength hydrogen-brittleness-resistant austenite alloy with mark of J75 and preparation method of high-strength hydrogen-brittleness-resistant austenite alloy

Also Published As

Publication number Publication date
CN102409258B (en) 2013-07-10

Similar Documents

Publication Publication Date Title
CN104328353B (en) A kind of rare-earth type 0Cr17Ni4Cu4Nb martensitic precipitations and preparation method thereof
CN104195458B (en) A kind of stainless steel hot-rolling plate of low relative permeability and preparation method thereof
CN109136652B (en) Nickel-based alloy large-section bar for nuclear power key equipment and manufacturing method thereof
CN109136653B (en) Nickel-based alloy for nuclear power equipment and manufacturing method of hot rolled plate of nickel-based alloy
CN101994066B (en) Deformation induced maraging stainless steel and machining process thereof
CN101709428A (en) Compound microalloy hot die steel with high heat resistance and preparation method thereof
CN104726746A (en) High-strength metastable beta-type titanium alloy bar and production method thereof
CN110592506B (en) GH4780 alloy blank and forging and preparation method thereof
CN101704169B (en) Welding wire for gas shielded welding of aging martensitic stainless steel
CN102676924A (en) Ultra-fine grained martensite steel plate and preparation method thereof
CN106756509B (en) A kind of high-temperature alloy structural steel and its Technology for Heating Processing
CN102560268B (en) Manufacturing method of ultra-low carbon high strength stainless steel thin pipe
CN102409258B (en) Structural homogeneity control method of boron-containing high strength hydrogen resistant brittle alloy
CN106702211B (en) A kind of method of optimization β γ TiAl alloy hot-working characters
CN107460370A (en) A kind of low-cost high-strength high-ductility metastable β Titanium-alloy and preparation method thereof
CN101886228A (en) Low carbon martensite aged stainless steel with high strength high toughness and high decay resistance performances
CN106011684A (en) High-strength and high-toughness stainless steel material and preparation method thereof
CN106939384B (en) High-tensile aluminium alloy rod
CN101654764A (en) Iron-nickel based highly elastic alloy, capillary pipe thereof and method for manufacturing capillary pipe
CN103725924A (en) Nickel alloy and manufacturing method thereof
CN107974542B (en) A kind of grain refining preparation method of nickel-saving type two phase stainless steel
CN107974632B (en) Austenite hot-work die steel and preparation method thereof
CN102994908A (en) Control method of ultra-low-carbon, high strength, hydrogen embrittlement-resistant alloy and non-metallic inclusion of austenitic alloy
CN106566953A (en) Corrosion-resisting alloy forge piece and production method thereof
CN108411156A (en) A kind of nearly β types high strength titanium alloy and preparation method thereof

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C14 Grant of patent or utility model
GR01 Patent grant