CN1044622C - High strength, nickel based and casted high temp. alloy - Google Patents
High strength, nickel based and casted high temp. alloy Download PDFInfo
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- CN1044622C CN1044622C CN96107076A CN96107076A CN1044622C CN 1044622 C CN1044622 C CN 1044622C CN 96107076 A CN96107076 A CN 96107076A CN 96107076 A CN96107076 A CN 96107076A CN 1044622 C CN1044622 C CN 1044622C
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Abstract
The present invention belongs to the technical field of alloy steel used at a high temperature, particularly to a high-strength and wear-resistance nickel-base high-temperature alloy component suitable for being used at a high temperature of 1350 DEG C. The nickel-base high-temperature alloy proposed by the present invention has the specific chemical components (wt%) of 0.10 to 0.40% of C, 25.0 to 38.0% of Cr, at most 2.0% of Mo, 10.0 to 18.0% of W, 0.01 to 3.0% of Hf, 0.01 to 3.05 of Al, at most 2.0% of Si, at most 2.0% of Mn, at most 10% of Fe, at most 0.20% of RE, and nickel as the rest. Compared with the prior art, the alloy of the present invention has the advantages of low cost and favorable performance, and particularly the property of the present invention is obviously better than that of the existing alloy when the present invention is used at a high temperature.
Description
The invention belongs to nickel-base alloy rings territory.Particularly be useful in the high-strength abrasion-proof nickel base superalloy parts that use under the high temperature (1350 ℃).
In modern industry, the high-strength temperature-resistant wear parts of the large-scale billet heating furnace of Steel Mill, as heat-resisting cushion block in hot-slide in the pusher-type furnace and the stepping fine strain of millet formula process furnace etc., all adopt the cobalt base superalloy material to make (as UMCo-50, PGUMCo-50 alloy COBAL 1973.3, P60-66).But this class alloy uses so be difficult to large-scale popularization owing to the shortage of cobalt resource and the costliness of price.In addition, Chinese patent CN85100649A has introduced a kind of Ni-Cr-W mold casting nickel base superalloy, though the cost of this alloy is lower than the UMCo-50 cobalt base alloy, still there are shortcomings such as the on the low side and thermal shock resistance difference of creep strength in this alloy when high temperature.Adopt parts such as the hot-slide of this alloy manufacturing and cushion block, the temperature non that often causes be heated blank because these parts are difficult to keep enough height for a long time under high temperature heavy load, thus have a strong impact on the quality of becoming a useful person.
The objective of the invention is to propose a kind of have higher use properties and the high strength anti abrasion nickel-base cast superalloy that the cost of material is low are at high temperature arranged.
According to purpose of the present invention, also consider simultaneously the effect of each alloying element, particularly add Hf and the Al effect in alloy, and for obtaining the stable austenite matrix effect of other alloying elements of solid solution in a large number, what therefore we were designed is to be the nickel base superalloy of fundamental element with nickel, its concrete alloy ingredient scope following (weight %) C0.10～0.40%, Cr 25.0～38.0%, Mo≤2.0%, W10.0～18.0%, Hf 0.01～3.0%, and Al 0.01～3.0%, Si≤2.0%, Mn≤2.0%, Fe≤10%, RE≤0.20, all the other are Ni.
The composition design of nickel-base cast superalloy of the present invention is to consider weak point in the existing superalloy, by the adjustment to alloy ingredient, obtains having more high-performance and economic nickel-base cast superalloy material.Therefore consider in alloy ingredient of the present invention that Cr is the decision element that improves the alloy oxidation-resistance, its add-on should be no less than 25%, W, Mo, Hf are important solution strengthening and carbide reinforced elements, particularly W has the fusing point that improves alloy significantly and the dual function of high temperature creep-resisting simultaneously.So the add-on of W should be 10～18%, the W too high levels is then easily separated out in the alloy and is harmful to the intensity reduction that makes material mutually.Mo and W add simultaneously the multiple strengthening effect, but the formed oxide compound of Mo liquefies when high temperature easily, may make the easy pitting corrosion of alloy material like this, so the Mo constituent content should be limited in lower level.The have clear improvement microstructure of alloy of Hf element, the particularly pattern of carbide and crystal boundary form, to improving the intensity of alloy, particularly the alloy flexible is improved decisive role, but consider the Cost And Performance of this alloy, so the content of Hf should be controlled in 0.01～3.0% scope.High temperature oxidation resistance is relatively poor to be the common drawback that contains high W, the existence of Mo alloy; when therefore improving Cr content; also should add an amount of Al; add an amount of Al and can play the generation that suppresses the alloy internal oxidation; with help alloy surface to form fine and close protective oxide layer; material itself is played a protective role, but Al too high levels or the low excessively performance of alloy of all can giving be brought bad effect.Therefore Al content should be controlled in 0.01～3.0% scope.Adding the formed carbide of carbon is the main reinforcement means of this alloy, when in this alloy, having stable primary carbide, can make this material have the excellent high-temperature wear resisting property, but carbon has the solid-liquid phase temperature of obvious reduction alloy, therefore the alloy of the present invention of life-time service under ultrahigh-temperature, carbon content should be limited in 0.10～0.40% scope.Can improve the antioxidant property that uses this alloy under low, middle temperature though add proper amount of rare-earth, use more than 1200 ℃, rare earth brings disadvantageous effect can for the oxidation-resistance of this alloy.So the rare earth adding quantity in alloy of the present invention, should be limited to according to the actual use temperature of material≤below 0.20%.Add Si and help improving the thermotolerance of alloy, but if content surpasses 2%, alloy toughness is produced detrimentally affect, Mn is the stabilizing element of austenite structure, and has the S fixed effect in the alloy, can reach abundant effect when the Mn amount is limited in 2%.So Si, Mn content range are all limit below 2%.Add Fe and replace Ni only for the consideration that reduces cost of alloy, when Fe content surpasses 10% with the high-temperature behavior of grievous injury alloy, so the present invention requires in the alloy Fe content few more good more.P and S are detrimental impurity, need be limited in below 0.04%.
The manufacture method of nickel-base cast superalloy of the present invention can adopt antivacuum stove or vacuum oven to smelt, and casting can adopt sand mold casting or casting method to carry out Foundry Production, and production method is similar to prior art, does not need special process production.It is low that nickel-base alloy of the present invention has cost compared with prior art, the cost of the ultrahigh-temperature abrasion-resistant cast nickel based alloy of this alloy and CN85100649A patent application is suitable, and the cost of comparing with the PGUMCo-50 cobalt base superalloy only is 2/5, but the use properties of this alloy, as high temperature endurance performance, thermal shock resistance and antioxidant property etc. all significantly is better than above-mentioned comparative alloy.
Embodiment
In the Chemical Composition scope of nickel-base casting alloy of the present invention, we smelt the alloy of five stove different content proportionings, and in order to contrast conveniently, we have also smelted 1 stove CN85100649A alloy and PGUMCo-50 alloy, smelt and all adopt the 25Kg vacuum induction furnace smelting.And essence casts sample, and production technique is identical.Table 1 compares for the composition of alloy of the present invention and comparative alloy, 1,2,3,4,5 are alloy ingredient of the present invention in table, 6,7 is the comparative alloy composition, table 2 is the enduring quality table of alloy embodiment of the present invention, table 3 is the comparison of 1000 hours creep rupture strengths, table 4 is heating---the water-cooled cycle index that produces visible crack for thermal shock resistance contrast, the numerical value in table.Table 5 is the contrast of oxidation weight loss (g/m2h).Above-mentioned experiment method is sample to be risen to 1250 ℃ of insulations by room temperature be chilled to room temperature with the electric furnace stove after 24 hours, the weightless situation of four circulation back duplicates.Comparing result according to above-mentioned table can find out that alloy of the present invention is better than comparative alloy with its performance of comparing of comparative alloy, especially uses under high-temperature condition, its performance obviously is better than comparative alloy.
The chemical ingredients contrast of table 1 the present invention and comparative alloy
| The alloy amount | C | Cr | Ni | Co | Fe | W | Mo | Hf | Al | Nb | Si | Mn | RE | S | P | |
| The present invention | 1 | 0.22 | 32.1 | Surplus | / | 0.35 | 17.2 | 0.8 | 0.05 | 0.9 | / | 0.31 | 0.61 | / | 0.025 | 0.03 |
| 2 | 0.28 | 29.1 | Surplus | / | 0.21 | 14.5 | 1.2 | 2.6 | 2.0 | / | 0.24 | 0.64 | / | 0.018 | 0.027 | |
| 3 | 0.30 | 27.9 | Surplus | / | 0.26 | 15.8 | / | 1.1 | 1.5 | / | 0.80 | 0.82 | 0.16 | 0.015 | 0.031 | |
| 4 | 0.40 | 34.6 | Surplus | / | 5.0 | 12.9 | 2.0 | 2.0 | 0.06 | / | 0.66 | 0.64 | / | 0.027 | 0.021 | |
| 5 | 0.27 | 30.2 | Surplus | / | 4.1 | 14.5 | / | 0.9 | 0.02 | / | 0.35 | 1.26 | 0.12 | 0.029 | 0.026 | |
| CN8 51 00649A | 0.44 | 33.1 | Surplus | / | 4.7 | 13.7 | / | / | / | / | 0.64 | 0.38 | 0.16* | |||
| PGUMCo-50 | 0.19 | 28.4 | / | 51.6 | 17.9 | / | / | / | / | 0.6 | 0.68 | 0.81 | ||||
* RE is the amount of allocating into
The enduring quality of table 2 embodiment of the invention
| Temperature ℃ | The embodiment sequence number | Rupture time, hour: divide | ||
| 8MPa | 18MPa | 38MPa | ||
| 1000 | 1 2 3 4 5 | / | / 10051:40 / / / | 1206:30 1218:10 1123:46 982:09 996:11 |
| 1100 | 1 2 3 4 5 | / | 1105:13 1402:090 1143:25 1096:10 1004:49 | 161:08 170:15 120:40 138:20 145:30 |
| 1200 | 1 2 3 4 5 | 1120:17 1268:10 1071:46 980:12 1001:06 | 96:46 101:07 89:42 80:10 86:03 | / |
Table 3 the present invention and similar alloy and cobalt base alloy 1000 advance creep rupture strength (MPa) contrast for a short time
| Temperature ℃ | The present invention | CN85100149A | PGUMCo-50 |
| 950 | 58 | 36 | 32 |
| 1000 | 38 | 24 | 25 |
| 1100 | 18 | 10 | 11 |
| 1200 | 8 | / | / |
Table 4 the present invention and the contrast of comparative alloy thermal shock resistance, table
Numerical value is for producing the heating-water-cooled cycle index of visible crack
| Temperature ℃ | The present invention | CN85100149A | PGUMCo-50 |
| 750 | ＞120 | 62 | 75 |
| 850 | 78 | 25 | 34 |
| 950 | 72 | 30 | 38 |
| 1050 | ＞110 | 42 | 46 |
Table 5 the present invention and comparative alloy oxidation weight loss amount (G/m2.h) contrast
| Temperature ℃ | 1000 | 1050 | 1100 | 1150 | 1200 | 1250 |
| The present invention | 0.20 | 0.31 | 0.37 | 0.61 | 1.21 | 3.01 |
| CN85100649A | 0.23 | 0.40 | 0.51 | 0.97 | 1.92 | 5.81 |
| PGUMCO-50 | 0.34 | 0.51 | 0.73 | 1.46 | 2.50 | 4.96 |
Claims (3)
1, a kind of nickel-base cast superalloy, the Chemical Composition that it is characterized in that this alloy is (weight %) C 0.10～0.40%, and Cr 25.0～38.0%, and W 10.0～18.0%, Hf 0.01～3.0%, and Al 0.01～3.0%, Si≤2.0%, Mn≤2.0%, Fe≤10%, all the other are Ni.
2,, it is characterized in that in the composition of this alloy, also containing Mo≤2.0% according to the described nickel-base cast superalloy of claim 1.
3,, it is characterized in that in the composition of this alloy, also containing RE≤0.2% according to the described nickel-base cast superalloy of claim 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN96107076A CN1044622C (en) | 1996-07-16 | 1996-07-16 | High strength, nickel based and casted high temp. alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN96107076A CN1044622C (en) | 1996-07-16 | 1996-07-16 | High strength, nickel based and casted high temp. alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1148097A CN1148097A (en) | 1997-04-23 |
| CN1044622C true CN1044622C (en) | 1999-08-11 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN96107076A Expired - Fee Related CN1044622C (en) | 1996-07-16 | 1996-07-16 | High strength, nickel based and casted high temp. alloy |
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| CN (1) | CN1044622C (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1048528C (en) * | 1997-09-12 | 2000-01-19 | 冶金工业部钢铁研究总院 | Nickel base deforming alloy target material for sputtering glass plating |
| JP3916484B2 (en) * | 2002-03-05 | 2007-05-16 | 独立行政法人科学技術振興機構 | Ni alloy heat resistant material excellent in high temperature oxidation resistance and method for producing the same |
| CN101935770B (en) * | 2010-08-31 | 2012-04-18 | 西安诺博尔稀贵金属材料有限公司 | Method for manufacturing aluminum and yttrium-containing multi-element nickel-based alloy ingot blank |
| CN101974708A (en) * | 2010-11-05 | 2011-02-16 | 钢铁研究总院 | Hot erosion resisting directionally solidified nickel-based cast superalloy |
| JP5998325B2 (en) * | 2011-03-29 | 2016-09-28 | 公立大学法人大阪府立大学 | Friction stir processing tool and friction stir processing method using the same |
| CN103436722A (en) * | 2013-07-30 | 2013-12-11 | 青岛新力通工业有限责任公司 | Production method of novel nickel-base furnace tube |
| CN103540803B (en) * | 2013-10-30 | 2016-03-02 | 钢铁研究总院 | A kind of high rigidity is without magnetic nichrome and preparation method thereof |
| CN103706778A (en) * | 2013-12-31 | 2014-04-09 | 大连福岛精密零部件有限公司 | Method for utilizing non-vacuum furnace to produce high temperature alloy parts of Stirling engine |
| CN108467973B (en) * | 2018-06-11 | 2020-04-10 | 江苏银环精密钢管有限公司 | Nickel-chromium-tungsten high-temperature alloy seamless tube for 700 ℃ ultra-supercritical boiler and manufacturing method thereof |
| CN114635059B (en) * | 2022-03-03 | 2023-02-10 | 北京北冶功能材料有限公司 | Ni-Cr-W-based alloy and preparation method thereof |
| CN117026015B (en) * | 2023-07-18 | 2024-02-13 | 大湾区大学(筹) | High-temperature-resistant alloy and preparation method and application thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN85100649A (en) * | 1985-04-01 | 1986-07-30 | 鞍山钢铁公司 | The ultrahigh-temperature abrasion-resistant cast nickel based alloy |
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1996
- 1996-07-16 CN CN96107076A patent/CN1044622C/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN85100649A (en) * | 1985-04-01 | 1986-07-30 | 鞍山钢铁公司 | The ultrahigh-temperature abrasion-resistant cast nickel based alloy |
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| CN1148097A (en) | 1997-04-23 |
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