CN106467955A - A kind of boride strengthening tube material with low-cost high-strength - Google Patents

A kind of boride strengthening tube material with low-cost high-strength Download PDF

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Publication number
CN106467955A
CN106467955A CN201610829488.8A CN201610829488A CN106467955A CN 106467955 A CN106467955 A CN 106467955A CN 201610829488 A CN201610829488 A CN 201610829488A CN 106467955 A CN106467955 A CN 106467955A
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tube material
boride
low
cost high
less
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严靖博
谷月峰
袁勇
赵新宝
鲁金涛
周永莉
黄锦阳
杨征
张醒兴
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Xian Thermal Power Research Institute Co Ltd
Huaneng Power International Inc
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Xian Thermal Power Research Institute Co Ltd
Huaneng Power International Inc
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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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • 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
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

A kind of boride strengthening tube material with low-cost high-strength, alloying component meets by mass percentage：C：0.2～0.5%, Cr：5～25%, Ni：20～25%, Co：0.5～3.0%, Mn：0.1%～0.5%, Si：0.1%～0.5%, W：5.0%～7.5%, Al：5～15%, Ti：0.5～2.5%, Nb：1.0～1.5%, B：0.5～1.2%, balance of Fe.As-cast Microstructure is mainly made up of with boride the alternatively distributed carbide of austenitic matrix and dendrite circle.Wherein, boride accounts for volume fraction and is not less than 5%, Cr23C6Volume fraction is not less than 10%.Tissue stabilization under the conditions of alloy high-temp prolonged heat exposure, precipitate size change is little, transgranular no obvious Second Phase Precipitation, and no New phase formation.

Description

A kind of boride strengthening tube material with low-cost high-strength
Technical field
The invention belongs to high temperature field of alloy steel is and in particular to a kind of boride strengthening with low-cost high-strength is new Tube material, is particularly well-suited to the portion of life-time service under the conditions of the superhigh temperature (more than 1000 DEG C) such as cracking furnace pipe in ethylene production Part, also apply be applicable to the parts such as coal burner nozzle in thermal power generation unit, the centrifuge in glass fiber industry, Yi Jiyi A little relatively low parts of temperature, such as HK-40 Tube at Hydrogen Reformer, nuclear power generating sets PWR steam generator pipe heat pipe and fired power generating unit pot Stove reheater etc..
Background technology
The carbide of certain volume fraction is the important leverage of austenitic heat-resistance steel elevated temperature strength performance, therefore at present in height The lower heat resisting steel using of temperature generally has higher Cr, C content, by forming large-sized nascent Cr in grain boundaries23C6And it is brilliant The interior secondary Cr separating out small and dispersed distribution23C6And make alloy obtain excellent elevated temperature strength performance.However, alloy in high temperature or Under low temperature condition of high ground stress during long service, Cr23C6Higher roughening is grown up and is inclined to and with the interface Cr element occurring Barren phenomenon all can cause very detrimental effect to the military service performance of alloy.People have carried out a series of trials in recent years, knot Fruit confirms that the interpolation of Nb element can be formed and the alternatively distributed NbC of chromium carbide in crystal boundary.Size is very steady at high temperature for the latter Fixed, inhibit Cr to a great extent simultaneously23C6Roughening grow up.Wherein, one of most representational achievement is to HP40 Add a small amount of Nb, Ti element in alloy (25Cr35Ni) cast tube, obtain having higher structure stability and rupture ductility HP40Nb alloy, so that material obtains longer service life.
But, this material exposes the unstable problem of tissue in use.Because alloy is using intermediate frequency sense Be difficult to avoid that when answering stove melting and can introduce certain Si element, and its can with alloy in (Nb, Ti) C reaction and and occur to G Phase (Ni16Nb6Si7) transformation, and ultimately result in the grain boundaries that the G phase of bulk is present in material, it is unfavorable that alloy plasticity is caused Impact.Additionally, (Nb, Ti) C also can cause intensity herein weak along with G phase and the lean Ni of basal body interface to during G phase in version Change, further adverse effect is caused to the mechanical behavior under high temperature of material.
The boride stability more excellent than having with Carbide Phases and higher hardness, because of its excellent anti-wear performance And receive significant attention as roll candidate materials.However, the addition of too high boron element can cause boron in alloy graining process Compound is existed with net pattern, and then causes " boron is crisp " phenomenon and bring harm to material military service performance, simultaneously also can be to material Machinability bring extreme influence.
Content of the invention
For overcoming the problems of the prior art, it is an object of the invention to provide a kind of boronation with low-cost high-strength Thing strengthens tube material, eliminates material " boron is crisp " phenomenon when superhigh temperature (1000 DEG C) is used above and material military service performance is caused Harm.Additionally, adding the Al of certain content to possess excellent antioxidation under ultra-high temperature condition to guarantee alloy in alloy With corrosion resistance.
In order to realize above goal of the invention, the technical solution adopted in the present invention is：
A kind of boride strengthening tube material with low-cost high-strength, this tube material composition meets such as by mass percentage Lower area requirement：C：0.2～0.5%, Cr：5～25%, Ni：20～25%, Co：0.5～3.0%, Mn：0.1%～0.5%, Si：0.1%～0.5%, W：5.0%～7.5%, Al：5～15%, Ti：0.5～2.5%, Nb：1.0～1.5%, B：0.5～ 1.2%, balance of Fe.
The present invention is further improved by, and the mass percent of B and C meets B/C=1.5～2.5, and works as Al mass hundred Divide than during less than 7%, Cr mass percent is not less than 22%.
The present invention is further improved by, and the as-cast structure of this tube material is mainly replaced with dendrite circle by austenitic matrix The carbide of distribution is constituted with boride；Wherein, boride accounts for volume fraction and is not less than 5%, Cr23C6Volume fraction is not less than 10%.
The present invention is further improved by, and this tube material is respectively higher than 90MPa in 1000 DEG C and 1100 DEG C of yield strengths And 45MPa, when 1050 DEG C, oxidation rate is less than 1.5 × 10-11g2cm-4s-1.
The present invention is further improved by, and this tube material adopts intermediate frequency furnace melting, and directly uses under as cast condition.
The present invention is further improved by, and when military service working condition pressure is more than 5MPa, this tube material adopts vacuum induction Stove melting, and it is aided with electroslag remelting process preparation.
Compared with prior art, the device have the advantages that：
1st, the present invention adds higher B element and by adjusting B, the ratio of C element on the basis of HK40 alloying component, promotees Enter to form (Nb, Ti) B and Cr23C6In the alternatively distributed tissue topography of grain boundaries, suppress continuous net-shaped Cr23C6With (Nb, Ti) B's Formed.Alloying component meets following area requirement by mass percentage：C：0.2～0.5%, Cr：5～25%, Ni：20～ 25%, Co：0.5～3.0%, Mn：0.1%～0.5%, Si：0.1%～0.5%, W：5.0%～7.5%, Al：5～15%, Ti：0.5～2.5%, Nb：1.0～1.5%, B：0.5～1.2%, balance of Fe.Alloy adopts intermediate frequency furnace melting, and in as cast condition Lower directly use, but when alloy military service working condition pressure is more than 5MPa, alloy should adopt vacuum induction melting, and is aided with electroslag Prepared by remelting processing.As-cast Microstructure is mainly by austenitic matrix and the alternatively distributed carbide of dendrite circle and boride structure Become.Wherein, boride and carbide account for volume fraction and are not lower than 5% and 10% respectively.
2nd, one of using boride as main hardening constituent, during alloy casting state, (Nb, Ti) B volume fraction is not less than 5% to alloy, Provide safeguard with hardness for possessing good intensity under alloy high-temp.
3rd, alloy microstructure assumes (Nb, Ti) B and Cr23C6It is alternately distributed pattern in grain boundaries, suppression is continuous net-shaped Cr23C6Formation with (Nb, Ti) B.Tissue stabilization, under the conditions of prolonged heat exposure, no new thing phase separates out, and tissue topography changes not Substantially.
4th, alloy, while guaranteeing good elevated temperature strength, decreases the constituent contents such as Ni, Cr, effectively reduces alloy former Material cost.
The 5th, higher B element is added on HK40 alloy (25Cr20Ni) component base, promotes nascent boride (Nb, Ti) The formation of B, and by adjusting B, the ratio of C element, promote to form (Nb, Ti) B and Cr23C6In the alternatively distributed tissue of grain boundaries Pattern is it is suppressed that continuous net-shaped Cr23C6With the formation of (Nb, Ti) B, eliminate material when superhigh temperature (1000 DEG C) is used above The harm that " boron is crisp " phenomenon causes to material military service performance.Additionally, adding the Al of certain content to exist to guarantee alloy in alloy Possess excellent antioxidation and corrosion resistance under ultra-high temperature condition.
6th, tube material of the present invention possesses good combination property and structure stability, precipitated phase chi under the conditions of prolonged heat exposure Very little change is little, transgranular no obvious Second Phase Precipitation, and no New phase formation.Alloy divides in 1000 DEG C and 1100 DEG C of yield strengths Not Gao Yu 90MPa and 45MPa, when 1050 DEG C oxidation rate be less than 1.8 × 10-11g2cm-4s-1.It is particularly well-suited to ethylene production In the superhigh temperature (more than 1000 DEG C) such as cracking furnace pipe under the conditions of life-time service part, also apply be applicable in thermal power generation unit The parts such as the centrifuge in coal burner nozzle, glass fiber industry, and the part that some temperature are relatively low, such as hydrogen manufacturing turns Change boiler tube, nuclear power generating sets PWR steam generator pipe heat pipe and thermal power unit boiler reheater etc..
Brief description
Fig. 1 is embodiment 1 alloy Analysis on Microstructure figure.
Fig. 2 is embodiment 1 alloy structure.
Fig. 3 is the element EDS point analysiss result at A in Fig. 2.
Fig. 4 is the element EDS point analysiss result at B in Fig. 2.
Specific embodiment
With reference to embodiment, the present invention is described in further detail.
Embodiment 1
The high temperature alloy cast tube material of the present embodiment, includes by mass percentage：C：0.2%, Cr：6%, Ni：24%, Co：3.0%, Mn：0.3%, Si：0.2%, W：5.0%, Al：15%, Ti：2.5%, Nb：1.5%, B：0.5%, balance of Fe.
The preparation method of the present embodiment comprises the following steps：
1) preparation of raw material：Composition includes by mass percentage：C：0.2%, Cr：6%, Ni：24%, Co：3.0%, Mn： 0.3%, Si：0.2%, W：5.0%, Al：15%, Ti：2.5%, Nb：1.5%, B：0.5%, balance of Fe.
2) melting step：The alloy of preparation is melted by all elements in addition to Si and Mn in mentioned component using induction furnace It is smelt alloy mother solution, molten steel reaches more than 1500 DEG C and adds silicon and manganese deoxidation afterwards, and controls the quality of P, S impurity element in mother solution The equal ＜ of degree 0.03%, cast of subsequently coming out of the stove after molten steel temperature reaches 1650 DEG C.
Embodiment 2
The high temperature alloy cast tube material of the present embodiment, includes by mass percentage：C：0.5%, Cr：25%, Ni：20%, Co：3.0%, Mn：0.1%, Si：0.3%, W：7.5%, Al：5%, Ti：0.5%, Nb：1.5%, B：0.9%, balance of Fe.
The preparation method of the present embodiment comprises the following steps：
1) preparation of raw material：Composition includes by mass percentage：C：0.5%, Cr：25%, Ni：20%, Co：3.0%, Mn： 0.1%, Si：0.3%, W：7.5%, Al：5%, Ti：0.5%, Nb：1.5%, B：0.9%, balance of Fe.
2) melting step：The alloy of preparation is melted by all elements in addition to Si and Mn in mentioned component using induction furnace It is smelt alloy mother solution, molten steel reaches more than 1500 DEG C and adds silicon and manganese deoxidation afterwards, and controls the quality of P, S impurity element in mother solution The equal ＜ of degree 0.03%, cast of subsequently coming out of the stove after molten steel temperature reaches 1630 DEG C.
Referring to table 1, the alloy material high-temperature behavior of embodiment 1-2 is tested respectively it is seen that alloy is in 1000- Possess excellent elevated temperature strength performance and antioxygenic property in the range of 1100 DEG C.Beta alloy is pressed in 1000 DEG C and 1100 DEG C Contracting yield strength is respectively higher than 90MPa and 45MPa, and when 1050 DEG C, oxidation rate is less than 1.8 × 10-11g2cm-4s-1.
Table 1 embodiment 1 and 2-in-1 gold high-temperature behavior test result
Referring to Fig. 1, embodiment 1 alloy microstructure morphology is observed it can be seen that except Ovshinsky in alloy structure Body presence biphase with chromium carbide is outer, also there is white chunks thing phase in grain boundaries and black shaft phase exists.Referring to Fig. 2, Fig. 3 And Fig. 4, two kinds of thing phases are carried out with EDS spot scan analysis, it is found that white thing phase is to have Nb, Ti enrichment of element, should be Nascent MC type richness Nb, Ti carbide.There are Nb, Ti, B to be enriched with black thing phase, show that it is mainly boride.
Embodiment 3
The high temperature alloy cast tube material of the present embodiment, includes by mass percentage：C：0.4%, Cr：20%, Ni：25%, Co：0.5%, Mn：0.2%, Si：0.1%, W：6.0%, Al：10%, Ti：1%, Nb：1%, B：1.0%, balance of Fe.
The preparation method of the present embodiment comprises the following steps：
1) preparation of raw material：Composition includes by mass percentage：C：0.4%, Cr：20%, Ni：25%, Co：0.5%, Mn： 0.2%, Si：0.1%, W：6.0%, Al：10%, Ti：1%, Nb：1%, B：1.0%, balance of Fe.
2) melting step：The alloy of preparation is melted by all elements in addition to Si and Mn in mentioned component using induction furnace It is smelt alloy mother solution, molten steel reaches more than 1500 DEG C and adds silicon and manganese deoxidation afterwards, and controls the quality of P, S impurity element in mother solution The equal ＜ of degree 0.03%, cast of subsequently coming out of the stove after molten steel temperature reaches 1650 DEG C.
Embodiment 4
The high temperature alloy cast tube material of the present embodiment, includes by mass percentage：C：0.5%, Cr：24%, Ni：22%, Co：1%, Mn：0.5%, Si：0.5%, W：6.5%, Al：6%, Ti：1.5%, Nb：1.2%, B：0.75%, balance of Fe.
The preparation method of the present embodiment comprises the following steps：
1) preparation of raw material：Composition includes by mass percentage：C：0.5%, Cr：24%, Ni：22%, Co：1%, Mn： 0.5%, Si：0.5%, W：6.5%, Al：6%, Ti：1.5%, Nb：1.2%, B：0.75%, balance of Fe.
2) melting step：The alloy of preparation is melted by all elements in addition to Si and Mn in mentioned component using induction furnace It is smelt alloy mother solution, molten steel reaches more than 1500 DEG C and adds silicon and manganese deoxidation afterwards, and controls the quality of P, S impurity element in mother solution The equal ＜ of degree 0.03%, cast of subsequently coming out of the stove after molten steel temperature reaches 1650 DEG C.
Embodiment 5
The high temperature alloy cast tube material of the present embodiment, includes by mass percentage：C：0.3%, Cr：20%, Ni：20%, Co：2%, Mn：0.4%, Si：0.4%, W：5.5%, Al：12%, Ti：2%, Nb：1%, B：0.75%, balance of Fe.
The preparation method of the present embodiment comprises the following steps：
1) preparation of raw material：Composition includes by mass percentage：C：0.5%, Cr：24%, Ni：22%, Co：1%, Mn： 0.5%, Si：0.0.5%, W：6.5%, Al：6%, Ti：1.5%, Nb：1.2%, B：0.75%, balance of Fe.
2) melting step：The alloy of preparation is melted by all elements in addition to Si and Mn in mentioned component using induction furnace It is smelt alloy mother solution, molten steel reaches more than 1500 DEG C and adds silicon and manganese deoxidation afterwards, and controls the quality of P, S impurity element in mother solution The equal ＜ of degree 0.03%, cast of subsequently coming out of the stove after molten steel temperature reaches 1650 DEG C.
This tube material adopts intermediate frequency furnace melting, and directly uses under as cast condition.When military service working condition pressure is more than 5MPa, should Tube material adopts vacuum induction melting, and is aided with electroslag remelting process preparation.
As-cast Microstructure of the present invention is mainly by austenitic matrix and the alternatively distributed carbide of dendrite circle and boride structure Become.Wherein, boride accounts for volume fraction and is not less than 5%, Cr23C6Volume fraction is not less than 10%.Alloy high-temp prolonged heat exposure Under the conditions of tissue stabilization, precipitate size change less, transgranular no obvious Second Phase Precipitation, and no New phase formation.This conjunction Gold is respectively higher than 90MPa and 45MPa in 1000 DEG C and 1100 DEG C of yield strengths, and when 1050 DEG C, oxidation rate is less than 1.8 × 10-11g2cm-4s-1.

Claims (6)

1. a kind of boride strengthening tube material with low-cost high-strength it is characterised in that：This tube material composition presses quality hundred Ratio is divided to meet following area requirement：C：0.2～0.5%, Cr：5～25%, Ni：20～25%, Co：0.5～3.0%, Mn： 0.1%～0.5%, Si：0.1%～0.5%, W：5.0%～7.5%, Al：5～15%, Ti：0.5～2.5%, Nb：1.0～ 1.5%, B：0.5～1.2%, balance of Fe.
2. a kind of boride strengthening tube material with low-cost high-strength according to claim 1 it is characterised in that：B Meet B/C=1.5～2.5 with the mass percent of C, and when Al mass percent is less than 7%, Cr mass percent is not less than 22%.
3. a kind of boride strengthening tube material with low-cost high-strength according to claim 1 it is characterised in that：Should The as-cast structure of tube material is mainly made up of with boride the alternatively distributed carbide of austenitic matrix and dendrite circle；Wherein, boron Compound accounts for volume fraction and is not less than 5%, Cr23C6Volume fraction is not less than 10%.
4. a kind of boride strengthening tube material with low-cost high-strength according to claim 1 it is characterised in that：Should Tube material is respectively higher than 90MPa and 45MPa in 1000 DEG C and 1100 DEG C of yield strengths, and when 1050 DEG C, oxidation rate is less than 1.5 ×10-11g2cm-4s-1.
5. a kind of boride strengthening tube material with low-cost high-strength according to claim 1 it is characterised in that：Should Tube material adopts intermediate frequency furnace melting, and directly uses under as cast condition.
6. a kind of boride strengthening tube material with low-cost high-strength according to claim 1 it is characterised in that：When When military service working condition pressure is more than 5MPa, this tube material adopts vacuum induction melting, and is aided with electroslag remelting process preparation.
CN201610829488.8A 2016-09-18 2016-09-18 A kind of boride strengthening tube material with low-cost high-strength Pending CN106467955A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115011879A (en) * 2022-06-23 2022-09-06 西北工业大学 Austenitic heat-resistant steel and heat treatment method thereof

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Publication number Priority date Publication date Assignee Title
JPS53108823A (en) * 1977-03-07 1978-09-22 Denki Jiki Zairiyou Kenkiyuush Magnetic alloy with rectangular hysterisis loop and method of making same
DE4210358A1 (en) * 1992-03-30 1993-10-07 Thyssen Edelstahlwerke Ag Device for avoiding the mucous membrane and respiration of soot in the exhaust gas of diesel engines
CN1179477A (en) * 1997-08-18 1998-04-22 冶金工业部钢铁研究总院 High-aluminium austenic heat resistant steel
CN101886230A (en) * 2010-05-18 2010-11-17 泰州市永昌冶金设备有限公司 High temperature steel

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53108823A (en) * 1977-03-07 1978-09-22 Denki Jiki Zairiyou Kenkiyuush Magnetic alloy with rectangular hysterisis loop and method of making same
DE4210358A1 (en) * 1992-03-30 1993-10-07 Thyssen Edelstahlwerke Ag Device for avoiding the mucous membrane and respiration of soot in the exhaust gas of diesel engines
CN1179477A (en) * 1997-08-18 1998-04-22 冶金工业部钢铁研究总院 High-aluminium austenic heat resistant steel
CN101886230A (en) * 2010-05-18 2010-11-17 泰州市永昌冶金设备有限公司 High temperature steel

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115011879A (en) * 2022-06-23 2022-09-06 西北工业大学 Austenitic heat-resistant steel and heat treatment method thereof
CN115011879B (en) * 2022-06-23 2024-02-06 西北工业大学 Austenitic heat-resistant steel and heat treatment method thereof

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