AU2013204206B2 - Steel Plate - Google Patents
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- AU2013204206B2 AU2013204206B2 AU2013204206A AU2013204206A AU2013204206B2 AU 2013204206 B2 AU2013204206 B2 AU 2013204206B2 AU 2013204206 A AU2013204206 A AU 2013204206A AU 2013204206 A AU2013204206 A AU 2013204206A AU 2013204206 B2 AU2013204206 B2 AU 2013204206B2
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Abstract
-25 A quenched steel plate is disclosed. The plate has a thickness of at least 6 mm, a martensite or tempered martensite 5 microstructure, and the following composition, in wt%: C: at least 0.3 Mn: < 0.8 Ti: < 0.08 Si: < 0.8 10 Ni: < 2.0 Cr: < 1.5 Mo: < 0.5 Cu: < 0.3 Al: < 0.12 15 Ca: < 0.005 B: < 0.005 P: < 0.040 V: < 0.10 S: < 0.02 20 Fe: balance and incidental impurities 42519221 (GHMatters) P91313.AU.1 12/04/13
Description
STEEL PLATE
The present invention relates to wear resistant quenched and tempered steel plate that is suitable for use in the mining and the construction industries in applications including wear liners, such as dump truck wear liners, chutes, earth moving buckets, cutting edges, and ground engaging tools.
Important properties for steel plate for the above applications include abrasion resistance, tensile strength, toughness, formability, and weldability.
The present invention provides an alternative steel plate to steel plate that is currently available in Australia that has an advantageous combination of the properties of abrasion resistance, tensile strength, toughness, formability and weldability.
The present invention is based on a realization from extensive research and development work that the use of low Mn concentrations (and low Carbon Equivalent (CET) values) is a basis for a quenched steel plate that has an advantageous combination of the properties of abrasion resistance, tensile strength, toughness, formability and weldability.
According to the present invention there is provided a quenched steel plate having a thickness of at least 6 mm, a martensite or tempered martensite microstructure, the following composition, in wt%: C: at least 0.3 Mn: < 0.8 Ti: < 0.08 Si: < 0.8 Ni: < 2.0 Cr: < 1.5 Mo: < 0.5 Cu: < 0.3 Al: < 0.12 Ca: < 0.005 B: < 0.005 P: < 0.040 V: < 0.10 S: < 0.02
Fe: balance and incidental impurities.
The term "incidental impurities" is understood herein to mean impurities that are the result of the steelmaking process and the feed materials used in the steelmaking process and are not deliberate additions to the composition and are not already in the list of elements. Sn is one such element.
The quenched steel plate may have any suitable a Carbon Equivalent (CET) value.
The quenched steel plate may have a CET value not exceeding 0.55 for plate thicknesses in the range 20 <t<= 60mm.
The quenched steel plate may have a CET value not exceeding 0.53 for plate thicknesses in the range 20 <t<= 60mm.
The quenched steel plate may have a CET value not exceeding 0.51 for plate thicknesses in the range of t <= 20mm.
The quenched steel plate may have a CET value not exceeding 0.49 for plate thicknesses in the range of t <= 20mm. CET provides a measure of the weldability of the steel and is determined as follows: CET (in wt%) = C + (Mn + Mo)/10 + (Cr + Cu)/20 + Ni/40
In any given situation, the selection of the steel chemistry of the quenched steel plate includes consideration of achieving required properties, such as any one or more of abrasion resistance, tensile strength, toughness, formability, and weldability, for an end use application on a cost effective basis .
The composition of the quenched steel plate may include less than 0.55 wt.% C.
The composition may include less than 0.5 wt.% C.
The composition may include less than 0.4 wt.% C.
The composition may include greater than 0.32 wt.% C. The composition may include greater than 0.35 wt.% C. The composition may include 0.32-0.5 wt.% C.
The composition may include 0.32-0.38 wt.% C.
The composition may include less than 0.7 wt.% Mn.
The composition may include less than 0.6 wt.% Mn.
The composition may include less than 0.4 wt.% Mn.
The composition may include less than 0.3 wt.% Mn.
The composition may include at least 0.15 wt.% Mn.
The composition may include greater than 0.55 wt.%
Mn.
The composition may include at least 0.001 wt.% Ti. The composition may include at least 0.01 wt.% Ti.
The composition may include 0.01-0.035 wt.% Ti.
The composition may include less than 0.035 wt.% Ti.
The composition may include less than 0.6 wt.% Ni.
The composition may include less than 0.5 wt.% Ni.
The composition may include less than 0.2 wt.% Ni.
The composition may include greater than 0.03 wt.%
Ni.
The composition may include less than 1.3 wt.% Cr.
The composition may include less than 1.0 wt.% Cr.
The composition may include greater than 0.2 wt.% Cr.
The composition may include less than 0.3 wt. % Mo.
The composition may include greater than 0.05 wt.%
Mo.
The composition may include less than 0.1 wt. % A1.
The composition may include less than 0.07 wt. % A1.
The composition may include less than 0.06 wt.% A1.
The composition may include greater than 0.01 wt.% Al.
The composition may include less than 0.005 wt.% Ca. The composition may include less than 0.0015 wt% Ca.
According to the present invention there is also provided a product made from the above-described steel plate.
The product may include, by way of example, wear liners such as dump truck wear liners.
According to the present invention there is also provided equipment for the mining and the construction industries that includes the above-described steel plate.
The equipment may include any one or more of dump trucks, chutes, earth moving buckets, and ground engaging tools.
The applicant has found that the above-described quenched steel plate has comparable or superior toughness, hardness, weldability, and formability to steel plate available in Australia.
The toughness of the above-described steel plate, after quenching and as measured in a Charpy impact test in a longitudinal direction with a 10 mm x 10 mm test sample, may be typically 15J at a test temperature of —40°C.
The toughness of the above-described steel plate, after quenching and as measured in a Charpy impact test in a transverse direction with a 10 mm x 10 mm test sample, may be typically 10J at a test temperature of —40°C.
The hardness of the above-described steel plate after quenching may be at least 450 Brinell through the thickness of the plate.
The hardness of the above-described steel plate after quenching may be at least 500 Brinell through the thickness of the plate.
The hardness of the above-described steel plate after quenching may be at least 570 Brinell through the thickness of the plate.
The hardness of the above-described steel plate after quenching may vary through the thickness of the plate, with the hardness at the surface of the plate being at least 570 Brinell.
The hardness of the above-described steel plate after quenching may be at least 570-630 Brinell through the thickness of the plate.
The Proof Stress of the above-described steel plate after quenching may be at least 1400 MPa.
The Proof Stress of the above-described steel plate after quenching may be at least 1450 MPa.
The tensile strength of the above-described steel plate after quenching may be at least 1800 MPa.
The tensile strength of the above-described steel plate after quenching may be at least 1900 MPa.
The thickness of the above-described steel plate may be at least 6 mm.
The thickness of the above-described steel plate may be 6-60 mm.
The thickness of the above-described steel plate may be 6-50 mm.
The thickness of the above-described steel plate may be 6-25 mm.
The above-described quenched steel plate may be manufactured by the following process: (a) continuously casting slabs of steel having a required composition; (b) hot rolling the slabs to form pattern plate having a required thickness, typically 6-60 mm or coil plate having a required thickness, typically 6-8 mm; (c) treating the hot rolled steel plate by: (i) heating the steel plate to the austenising temperature range and holding the steel plate in the temperature range for a predetermined time; and (ii) quenching the steel plate, typically with water sprays.
The objective of the above-described heat treatment step (c) is to form a martensite or tempered martensite microstructure.
Treatment step (c) may include a further step of tempering the quenched steel plate as required at a predetermined temperature.
The tempering temperature may be at least 150°C.
The tempering temperature may be in a range of 150200 °C.
In general terms, one quenched and tempered steel plate in accordance with the present invention is made from steel comprising 0.38-0.42% C, 0.30-0.34% Mn, 0.20-0.30% Mo, 0.02-0.06% Al, 0.02-0.03% Ti, 0-7-1.3% Cr, 0.2-0.6% Ni, 0.010.02% P and 0.001-0.002% B by quenching the plate from an austenising temperature and tempering the quenched plate under mild conditions, with the plate having a hardness of 600 Brinell and a Yield Stress of at least 1800 MPa and a Tensile Strength of at least 2000 MPa.
More particularly, the quenched and tempered steel plate in accordance with the present invention is made from steel comprising 0.38-0.42% C, 0.30-0.34% Mn, 0.20-0.30% Mo, 0.02-0.06% Al, 0.02-0.03% Ti, 0-7-1.3% Cr, 0.2-0.6% Ni, 0.010.02% P and 0.001-0.002% B by quenching the plate from an austenising temperature of around 900°C and tempering the quenched plate at 150-200°C for 30 minutes, with the plate having a hardness of 600 Brinell and a Yield Stress of at least 1800 MPa and a Tensile Strength of at least 2000 MPa.
The applicant has carried out extensive research and development work in the field of wear resistant quenched and tempered steel plate and made the invention as part of that work.
The work included research and development work as described below.
Samples of steel comprising 0.38-0.42% C, 0.30-0.34% Mn, 0.20-0.30% Mo, 0.02-0.06% Al, 0.02-0.03% Ti, 0-7-1.3% Cr, 0.2-0.6% Ni, 0.01-0.02% P and 0.001-0.002% B. in thicknesses ranging from 12-50 mm (specifically 12, 16, 20, 25, 32, 40, and 50 mm) were manufactured from the steel composition by quenching from an austenising temperature of around 900°C and lightly tempering the quenched plate at 150-200°C for 30 minutes.
Samples of quenched steel plates made to the above mentioned chemistry limits were tested for tensile properties, impact properties, formability and hardness .
The toughness of 12 mm, 20 mm, 32 mm and 50 mm thick samples of the quenched and lightly tempered steel plates having the above compositions was tested in standard Charpy toughness tests in accordance with Australian Standard AS 1544.2. Tensile testing was carried out on the 12 and 20 mm plates.
The results of the test work are summarized in Table 2. Table 2: Tensile and Charpy impact results
Thickness PS (MPa) UTS (MPa) Elongation% I Cv L Θ - I Cv T Θ -
4 0 ° C 4 0 ° C
12mm 1483 2084 6 Ave 15J Ave 11J
20mm 1406 2073 7 Ave 16J Ave 11J
32mm Ave 15J Ave 15J
50mm Ave 10J Ave 11J
Formability was assessed using a 3 point bend test, and the results are shown in Table 3.
Table 3: Bend tests
Thickness Transverse Longitudinal Bent angle
Radius Result Radius Result 12mm 3.6t/dia Failed 4.25t/dia Passed 90° 12mm 4.25t/dia Passed 5.3t/dia Passed 90° 20mm 5t/dia Passed Na na 90°
Through hardening characteristics are shown in Figure 1 for the 32 mm plate, which showed through hardening above 600 BH.
Table 4 shows the variation in sub-surface hardness for 12 mm, 16 mm, 20 mm, 25 mm, 32 mm, 40 mm and 50 mm quenched plates, where all plates were within a range of 575-620 BH.
Table 4: Sub surface hardiness
During the course of the work, the applicant has developed the following alloy design philosophy that is based on the use of low Mn concentrations and a low Carbon Equivalent (CET) value.
Low Mn (low CET) Alloy Design Philosophy
Key features of the low Mn (low CET) alloy design are as follows : 1. Low Mn is essential since it imparts: a. Improved weldability (via low CET Carbon Equivalent) since Mn exerts a relatively strong penalty for the CET value. The improved weldability is primarily evident in lower weld HAZ cracking sensitivity and reduced requirements for minimum preheat and weld interpass temperature restrictions. b. Reduced centreline segregation (arising from Mn enrichment in continuously cast slab production) which directly reduces susceptibility to delayed cracking after gas cutting (especially in the hardened quenched condition). c. Reduced microstructural banding (arising from Mn microsegregation) which directly enhances isotropic bending performance, Charpy toughness and through thickness tensile ductility. d. Smaller sulphide inclusions at a given sulphur content in the steel so that higher Charpy toughness levels, improved bendability and through thickness tensile ductility are attainable in comparison to high Mn steels. This means that high Mn steels must exercise more severe limitations on both the S content and inclusion morphology than is necessary for low Mn steels to produce equivalent toughness. 2 . Ti additions may be used for: a. Combining N in the steel as TiN to minimise the risk for transverse cracking that might otherwise arise from the embrittling formation of grain boundary precipitates of AIN or BN during continuous casting and thereby ensure excellent surface quality. b. Combining N so that boron can be effective in the enhancement of through hardening of the plate during the quenching cycle of the plate heat treatment. c. Partially combining with MnS inclusions to increase their deformation resistance during hot rolling and thereby optimise toughness, bendability and through thickness tensile ductility. d. Provides control of austenite grain size in the austenitising phase of the Q&T heat treatment cycle and in the coarse grained weld heat affected zone thereby enhancing both parent metal plate and weld zone toughness . 3. V additions may be used for: a. Assisting in the risk abatement of delayed cracking in the hardened plate through H trapping mechanisms. b. Controlling the resistance to high temperature softening in wear applications where temperature increases due to abrasive wear, hot environments or the handling of hot materials such as coke can elevate the steel plate temperatures. c. Controlling the balance of toughness and strength required for high strength structural Q&T plates via secondary hardening behaviour. Mo additions may also be used in conjunction with V for this purpose. 4. Ni additions may be used for enhancing low temperature plate toughness . 5. Cr additions may be used as a primary alloying element for ensuring adequate hardenability for through hardening of plates during heat treatment. It is preferred to Mn because of its relatively lower segregating tendencies in steelmaking and its much smaller penalty to the CET carbon equivalent (weldability) than Mn.
Basic Method Applied to Low CET Quench and Temper Wear Plates 1. Select minimum C content required to achieve a target BHN in quenched condition (after J. M. Hodge and M. A. Orehoski, "Relationship Between Hardenability and Percentage of Martensite in Some Low Alloy Steels," J. ΑΙΜΕ, 167 (1946), p. 627.). 2. Select primary aim chemical analysis (based on the above low Mn (and low CET) alloy design philosophy) for the required critical plate thickness consideration (maximum plate thickness to be produced from the selected chemistry range).
This key step determines the basic disposition of the steel in relation to weldability (preheat levels, crack resistance), delayed cracking resistance after gas cutting, bendability and through thickness tensile ductility. 3. Adjust critical steelmaking parameters, including primary aim chemical analysis to further tailor specific requirements such as for isotropic and low temperature toughness, heat resistance and optimised manufacturability.
Basic Method Applied to Tempered Structural Steel
Plates 1. Select aim C content required to optimise strength, weldability, and toughness requirements. For a 690 MPa (750 MPa tensile strength), this will generally be in the range of 0.12-0.17% C. 2 . For nominated C level, select primary aim chemical analysis (based on the above low Mn (and low CET) alloy design philosophy) for the required critical plate thickness consideration (maximum plate thickness to be produced from the selected chemistry range). 3. Adjust critical steelmaking parameters, including primary aim chemical analysis to further tailor specific requirements such as for isotropic and low temperature toughness, through tensile ductility, heat resistance and optimised manufacturability.
The research and development work carried out using the above-described low Mn (and low CET) approach included the development and assessment of 400, 450 and 500 BH, quench and tempered wear grades, and structural quench and tempered grades with minimum yield strength of 690 MPa (750 MPa tensile strength).
Assessment work carried out included, but was not limited to; 1. Surface hardness and through thickness hardness profiles. 2. Tensile properties to determine yield, tensile strength and elongation. 3. Bend tests to quantify formability performance. 4. Weldability assessment, which included, but was not limited to: i. Weld bead-on-plate (BOP) tests to determine the parent, heat affected zone (HAZ) and fusion line hardness, ii. Transverse weld tensile properties, iii. Weld HAZ Charpy V notch impact properties to determine the toughness of weld fusion line and HAZ at various distances from fusion line, iv. Cold cracking resistance was determined using RRC (Ridged Restraint Cracking) weld tests.
Typical chemistries of grades developed via the low Mn philosophy are shown in Table 1.
Table 1: Typical chemical composition of quench and tempered grades based on low Mn design.
In addition to the above grades, the applicant has developed a 600 Brinell Hardness grade via the low Mn philosophy. This grade is particularly suitable for use in the manufacture of armored vehicles and in hard rock mining applications. As described above, the grade is made from steel comprising 0.38-0.42% C, 0.30-0.34% Mn, 0.20-0.30% Mo, 0.020.06% Al, 0.02-0.03% Ti, 0-7-1.3% Cr, 0.2-0.6% Ni, 0.01-0.02% P and 0.001-0.002% B. Steel plate in thicknesses ranging from 1250 mm (specifically 12, 16, 20, 25, 32, 40, and 50 mm) is manufactured from the steel composition by quenching from an austenising temperature of around 900°C and tempering the quenched plate at 150-200°C for 30 minutes. The plate has a hardness of 600 Brinell and a Yield Stress of 1800 MPa and a Tensile Strength of 2000 MPa.
Many modifications may be made to the present invention described above without departing from the spirit and scope of the invention.
Claims (28)
1. A quenched steel plate having a thickness of at least 6 mm, a martensite or tempered martensite microstructure, the following composition, in wt%, C: at least 0.3 Mn: < 0.8 Ti: < 0.08 Si: < 0.8 Ni: < 2.0 Cr: < 1.5 Mo: < 0.5 Cu: < 0.3 Al: < 0.12 Ca: < 0.005 B: < 0.005 P: < 0.040 V: < 0.10 S: < 0.02 Fe: balance and incidental impurities.
2. The steel plate defined in claim 1 having a CET value not exceeding 0.55 for plate thicknesses in the range 20 <t<= 60mm.
3. The steel plate defined in claim 1 having a CET value not exceeding 0.51 for plate thicknesses in the range of t <= 20mm.
4. The steel plate defined in any one of the preceding claims wherein the carbon concentration in the composition is less than 0.55 wt. % .
5. The steel plate defined in any one of the preceding claims wherein the carbon concentration in the composition is less than 0.5 wt.%.
6. The steel plate defined in any one of the preceding claims wherein the carbon concentration in the composition is greater than 0.32 wt. %.
7. The steel plate defined in any one of the preceding claims wherein the manganese concentration in the composition is less than 0.7 wt.%.
8. The steel plate defined in any one of the preceding claims wherein the manganese concentration in the composition is less than 0.3 wt.%.
9. The steel plate defined in any one of the preceding claims wherein the manganese concentration in the composition is greater than 0.15 wt.%.
10. The steel plate defined in any one of the preceding claims wherein the titanium concentration in the composition is at least 0.01 wt.%.
11. The steel plate defined in any one of the preceding claims wherein the titanium concentration in the composition isO.01-0.035 wt.%.
12. The steel plate defined in any one of the preceding claims wherein the nickel concentration in the composition is less than 0.2 wt. %.
13. The steel plate defined in any one of the preceding claims wherein the chromium concentration in the composition is less than 1.0 wt. %.
14. The steel plate defined in any one of the preceding claims wherein the molybdenum concentration in the composition is less than 0.3 wt. % .
15. The steel plate defined in any one of the preceding claims wherein the calcium concentration in the composition is less than 0.0015 wt.%.
16. The steel plate defined in any one of the preceding claims having a toughness, after quenching and as measured in a Charpy impact test in a longitudinal direction with a 10 mm x 10 mm test sample, of typically 15J at a test temperature of —40°C.
17. The steel plate defined in any one of the preceding claims having a toughness, after quenching and as measured in a Charpy impact test in a transverse direction with a 10 mm x 10 mm test sample, of typically 10J at a test temperature of —40°C.
18. The steel plate defined in any one of the preceding claims having a hardness after quenching of at least 570 Brinell through the thickness of the plate.
19. The steel plate defined in any one of claims 1 -17 wherein the hardness of the steel plate after quenching varies through the thickness of the plate, with the hardness at the surface of the plate being at least 570 Brinell.
20. The steel plate defined in any one of the preceding claims having a tensile strength after quenching of at least 1800 MPa.
21. The steel plate defined in any one of the preceding claims having a thickness of 6-60 mm.
22. A process for manufacturing the steel plate defined in any one of the preceding claims includes: (a) continuously casting slabs of steel having a required composition; (b) hot rolling the slabs to form pattern plate or coil plate having a required thickness; (c) treating the hot rolled steel plate by: (i) heating the steel plate to the austenising temperature range and holding the steel plate in the temperature range for a predetermined time; and (ii) quenching the steel plate.
23. The process defined in claim 22 wherein treatment step (c) includes tempering the quenched steel plate at a predetermined temperature.
24. A quenched and tempered steel plate made from steel comprising 0.38-0.42% C, 0.30-0.34% Mn, 0.20-0.30% Mo, 0.020.06% Al, 0.02-0.03% Ti, 0-7-1.3% Cr, 0.2-0.6% Ni, 0.01-0.02% P and 0.001-0.002% B by quenching the plate from an austenising temperature and tempering the quenched plate under mild conditions, with the plate having a hardness of 600 Brinell and a Yield Stress of at least 1800 MPa and a Tensile Strength of at least 2000 MPa.
25. A product made from the steel plate defined in any one of claims 1-21.
26. The product defined in claim 25 includes a wear liner such as a dump truck wear liner.
27. Equipment for the mining and the construction industries that includes the steel plate defined in any one of claims 1-21.
28. The equipment defined in claim 27 includes any one or more of dump trucks, chutes, earth moving buckets, and ground engaging tools.
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| AU2013204206A AU2013204206B2 (en) | 2012-10-19 | 2013-04-12 | Steel Plate |
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| AU2012904577 | 2012-10-19 | ||
| AU2012904577A AU2012904577A0 (en) | 2012-10-19 | Steel Plate | |
| AU2013204206A AU2013204206B2 (en) | 2012-10-19 | 2013-04-12 | Steel Plate |
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| AU2013204206A1 AU2013204206A1 (en) | 2014-05-08 |
| AU2013204206B2 true AU2013204206B2 (en) | 2016-09-15 |
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| SI3719148T1 (en) * | 2019-04-05 | 2023-06-30 | Ssab Technology Ab | High-hardness steel product and method of manufacturing the same |
| CN115386797B (en) * | 2022-08-29 | 2023-08-22 | 西安建筑科技大学 | Non-quenched and tempered steel for automobiles and processing method thereof |
| CN115449697B (en) * | 2022-09-29 | 2023-04-25 | 南通高欣耐磨科技股份有限公司 | Ceramic particle reinforced high manganese steel-based composite material hammer and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005256169A (en) * | 2004-02-12 | 2005-09-22 | Jfe Steel Kk | Wear resistant steel sheet having excellent low temperature toughness and production method therefor |
| CN102234743A (en) * | 2010-04-23 | 2011-11-09 | 宝山钢铁股份有限公司 | Low carbon martensite steel plate and production method |
| US20120132322A1 (en) * | 2010-11-30 | 2012-05-31 | Kennametal Inc. | Abrasion resistant steel, method of manufacturing an abrasion resistant steel and articles made therefrom |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005256169A (en) * | 2004-02-12 | 2005-09-22 | Jfe Steel Kk | Wear resistant steel sheet having excellent low temperature toughness and production method therefor |
| CN102234743A (en) * | 2010-04-23 | 2011-11-09 | 宝山钢铁股份有限公司 | Low carbon martensite steel plate and production method |
| US20120132322A1 (en) * | 2010-11-30 | 2012-05-31 | Kennametal Inc. | Abrasion resistant steel, method of manufacturing an abrasion resistant steel and articles made therefrom |
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