EP0445519A1 - Acier résistant à l'usure pour utilisation à des températures intermédiaires et à la température ambiante - Google Patents

Acier résistant à l'usure pour utilisation à des températures intermédiaires et à la température ambiante Download PDF

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Publication number
EP0445519A1
EP0445519A1 EP91101082A EP91101082A EP0445519A1 EP 0445519 A1 EP0445519 A1 EP 0445519A1 EP 91101082 A EP91101082 A EP 91101082A EP 91101082 A EP91101082 A EP 91101082A EP 0445519 A1 EP0445519 A1 EP 0445519A1
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EP
European Patent Office
Prior art keywords
temperature
wear
room
brinell hardness
resistant steel
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.)
Withdrawn
Application number
EP91101082A
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German (de)
English (en)
Inventor
Nobuo C/O Nkk Corp. Shikanai
Tetsuya C/O Nkk Corp. Sanpei
Kazunori C/O Nkk Corp. Yako
Yasunobu C/O Nkk Corp. Kunisada
Kenji C/O Nkk Corp. Hirabe
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.)
JFE Engineering Corp
Original Assignee
NKK Corp
Nippon Kokan Ltd
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Publication date
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Publication of EP0445519A1 publication Critical patent/EP0445519A1/fr
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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
    • C22C38/04—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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon

Definitions

  • the present invention relates to a wear-resistant steel having a high hardness in an intermediate temperature region and a room-temperature region.
  • a wear-resistant steel is used as a material for portions exposed to serious wear in an industrial machine and a transportation machine such as a power shovel, a bulldozer, a hopper or a bucket and parts thereof. Wear resistance of steel can be improved by increasing hardness of the steel.
  • a wear-resistant steel having a high room-temperature hardness is available in all cases.
  • the prior arts 1 to 3 have the following problems: A wear-resistant steel is used also as a material for a machine and parts thereof for treating slag at a temperature within an intermediate temperature region of from about 300 to about 400°C in a slag yard.
  • a wear-resistant steel used as such a material should preferably have a Brinell hardness(HB) at a room-temperature of at least 250, a Brinell hardness at a temperature of about 300°C of at least 90% of its room-temperature Brinell hardness, and a Brinell hardness at a temperature of about 400°C of at least 70% of its room-temperature Brinell hardness.
  • HB Brinell hardness
  • wear-resistant steels of the prior arts 1 to 3 While it is possible to improve wear resistance at a temperature within a room temperature region, it is impossible to improve wear resistance at a temperature within an intermediate temperature region of from about 300 to about 400°C.
  • the wear-resistant steels of the prior arts 1 to 3 are not satisfactory in terms of wear resistance when used as a material for a machine and parts thereof employed at a temperature within an intermediate temperature region.
  • a conceivable measure is to largely increase a room-temperature hardness of steel, taking account of the decrease in hardness at a temperature within an intermediate temperature region.
  • a room-temperature hardness of steel is increased excessively, however, ductility, toughness, workability and weldability of the steel are deteriorated.
  • a wear-resistant steel for the intermediate and room temperature service which has a Brinell hardness at a room-temperature of at least 250, and has a Brinell hardness at a temperature of about 300°C of at least 90% of its room-temperature Brinell hardness, and a Brinell hardness at a temperature of about 400°C of at least 70% of its room-temperature Brinell hardness, the last two Brinell hardnesses being available without largely increasing its room-temperature Brinell hardness, but such a wear-resistant steel for the intermediate and room temperature service has not as yet been proposed.
  • An object of the present invention is therefore to provide a wear-resistant steel for the intermediate and room temperature service, which has a Brinell hardness at a room-temperature of at least 250, and has a Brinell hardness at a temperature of 300°C of at least 90% of its room-temperature Brinell hardness and a Brinell hardness at a temperature of 400°C of at least 70% of its room-temperature Brinell hardness, the last two Brinell hardnesses being available without largely increasing its room-temperature Brinell hardness.
  • a wear-resistant steel for the intermediate and room temperature service which has a Brinell hardness at a room-temperature of at least 250, a Brinell hardness at a temperature of 300°C of at least 90% of its room-temperature Brinell hardness, and a Brinell hardness at a temperature of 400°C of at least 70% of its room-temperature Brinell hardness, characterized by consisting essentially of:
  • the wear-resistant steel for the intermediate and room temperature service of the present invention may additionally contain at least one element selected from the group (A) consisting of:
  • the wear-resistant steel for the intermediate and room temperature service of the present invention may additionally contain at least one element selected from the above-mentioned group (A) and at least one element selected from the above-mentioned group (B).
  • Fig. 1 is a graph illustrating the relationship between a silicon content and a Brinell hardness (HB) in a wear-resistant steel.
  • the present invention was made on the basis of the above-mentioned findings, and the wear-resistant steel for the intermediate and room temperature service of the present invention consists essentially of:
  • the wear-resistant steel for the intermediate and room temperature service of the present invention may additionally contain at least one element selected from the group (A) consisting of:
  • the wear-resistant steel for the intermediate and room temperature service of the present invention may additionally contain at least one element selected from the above-mentioned group (A) and at least one element selected from the above-mentioned group (B).
  • the chemical composition of the wear-resistant steel for the intermediate and room temperature service of the present invention is limited within a range as described above for the following reasons.
  • Carbon is an element which exerts an important effect on hardness of steel.
  • a Brinell hardness (HB) at a room-temperature of at least 250 is not available.
  • a carbon content of over 0.40 wt.% on the other hand, a room-temperature Brinell hardness becomes excessively high to result in deterioration of ductility, toughness, workability and weldability of steel.
  • the carbon content should therefore be limited within a range of from 0.08 to 0.40 wt.%.
  • Silicon has a function of increasing hardness of steel in an intermediate temperature region without increasing its room-temperature hardness. However, with a silicon content of under 0.8 wt.%, a desired effect as mentioned above is not available.
  • a silicon content and a Brinell hardness (HB) in a wear-resistant steel was investigated. More particularly, for test pieces of a hardened wear-resistant steel having a thickness of 20 mm, which contained 0.3 wt.% carbon, 0.7 wt.% manganese, 0.9 wt.% chromium and silicon in a certain amount, a Brinell hardness (HB) was measured for each test piece at a room-temperature, 300°C, 400°C and 500°C with the silicon content varying within a range of from about 0.4 to about 2.0 wt.%. The results are shown in Fig. 1.
  • the mark “o” represents a Brinell hardness at a room-temperature of the test piece
  • the mark “ ⁇ ” represents a Brinell hardness at a temperature of 300°C of the test piece
  • the mark “ ⁇ ” represents a Brinell hardness at a temperature of 400°C of the test piece
  • the mark “ ⁇ ” represents a Brinell hardness at a temperature of 500°C of the test piece.
  • the test pieces showed a Brinell hardness at a room-temperature of about 500 almost constantly irrespective of the increase in the silicon content.
  • the test pieces showed a Brinell hardness at a temperature of 300°C of at least 450, i.e., about 90% of its room-temperature Brinell hardness by increasing the silicon content to at least 0.8 wt.%.
  • the test pieces showed a Brinell hardness at a temperature of 400°C of at least 350, i.e., about 70% of its room-temperature Brinell hardness by increasing the silicon content to at least 0.8 wt.%.
  • the test pieces showed a Brinell hardness at a temperature of 500°C also increased, though on a relatively low level, by increasing the silicon content to at least 0.8 wt.%.
  • ⁇ -ferrite is produced in the steel structure, and this may cause degradation of a room-temperature hardness of steel, and the manufacturing cost of steel becomes higher.
  • the silicon content should therefore be limited within a range of from 0.8 to 2.5 wt.%.
  • Manganese has a function of improving hardenability of steel. However, with a manganese content of under 0.1 wt.%, a desired effect as mentioned above is not available. With a manganese content of over 2.0 wt.%, on the other hand, weldability of steel is degraded, and the manufacturing cost of steel becomes higher. The manganese content should therefore be limited within a range of from 0.1 to 2.0 wt.%.
  • Copper has a function of improving hardenability of steel.
  • copper is additionally added as required.
  • a copper content of under 0.1 wt.% a desired effect as mentioned above is not available.
  • a copper content of over 2.0 wt.% on the other hand, hot workability of steel is degraded.
  • the copper content should therefore be limited within a range of from 0.1 to 2.0 wt.%.
  • Nickel has a function of improving hardenability and low-temperature toughness of steel. In the wear-resistant steel of the present invention, therefore, nickel is additionally added as required. However, with a nickel content of under 0.1 wt.%, a desired effect as mentioned above is not available. With a nickel content of over 10.0 wt.%, on the other hand, the manufacturing cost of steel becomes higher. The nickel content should therefore be limited within a range of from 0.1 to 10.0 wt.%.
  • Chromium has a function of improving hardenability of steel.
  • chromium is additionally added as required.
  • a desired effect as mentioned above is not available.
  • a chromium content of over 3.0 wt.% on the other hand, weldability of steel is degraded, and the manufacturing cost of steel becomes higher.
  • the chromium content should therefore be limited within a range of from 0.1 to 3.0 wt.%.
  • molybdenum has a function of improving hardenability of steel.
  • molybdenum is additionally added as required.
  • a molybdenum content of under 0.1 wt.% a desired effect as mentioned above is not available.
  • a molybdenum content of over 3.0 wt.% on the other hand, weldability of steel is degraded and the manufacturing cost of steel becomes higher.
  • the molybdenum content should therefore be limited within a range of from 0.1 to 3.0 wt.%.
  • Boron has a function of improving hardenability of steel with a slight content.
  • boron is additionally added as required.
  • a boron content of under 0.0003 wt.%, a desired effect as mentioned above is not available.
  • a boron content of over 0.0100 wt.% on the other hand, weldability and hardenability of steel are degraded.
  • the boron content should therefore be limited within a range of from 0.0003 to 0.0100 wt.%.
  • Niobium has a function of improving hardness of steel through precipitation hardening. In the wear-resistant steel of the present invention, therefore, niobium is additionally added as required. However, with a niobium content of under 0.005 wt.%, a desired effect as mentioned above is not available. With a niobium content of over 0.100 wt.%, on the other hand, weldability of steel is degraded. The niobium content should therefore be limited within a range of from 0.005 to 0.100 wt.%.
  • vanadium has a function of improving hardness of steel through precipitation hardening.
  • vanadium is additionally added as required.
  • a vanadium content of under 0.01 wt.% a desired effect as mentioned above is not available.
  • a vanadium content of over 0.10 wt.% on the other hand, weldability of steel is degraded.
  • the vanadium content should therefore be limited within a range of from 0.01 to 0.10 wt.%.
  • titanium has a function of improving hardness of steel through precipitation hardening.
  • titanium is additionally added as required.
  • a titanium content of under 0.005 wt.% a desired effect as mentioned above is not available.
  • a titanium content of over 0.100 wt.% weldability of steel is degraded.
  • the titanium content should therefore be limited within a range of from 0.005 to 0.100 wt.%.
  • a slab of a wear-resistant steel having the above-mentioned chemical composition may be hot-rolled to prepare a steel sheet, and the thus prepared steel sheet may be subjected to heat treatments including a hardening treatment, a tempering treatment, an ageing treatment and a stress relieving treatment. Hardness and toughness of the steel sheet can further be improved by the application of these heat treatments thereto.
  • Ingots of the wear-resistant steel of the present invention having the chemical compositions within the scope of the present invention as shown in Table 1, and ingots of a wear-resistant steel for comparison having the chemical compositions outside the scope of the present invention as shown also in Table 1, were melted in a melting furnace, and then cast into slabs.
  • the resultant slabs were then hot-rolled to prepare samples of the wear-resistant steel of the present invention (hereinafter referred to as the "samples of the invention") Nos. 1 to 13 having a thickness of 15 mm, and samples of the wear-resistant steel for comparison outside the scope of the present invention (hereinafter referred to as the "samples for comparison") Nos. 1 to 4 also having a thickness of 15 mm.
  • the samples of the invention Nos. 1 to 4 and 6 to 13, and the samples for comparison Nos. 1 to 3 were subjected to any one of the following heat treatments as shown in the column of "heat treatment" in Table 1.
  • the sample of the invention No. 5 and the sample for comparison No. 4 were maintained in the as-rolled state without being subjected to any heat treatment.
  • Each value of percentages shown in the parentheses in the subcolumns of "at 300°C” and “at 400°C” presents a ratio of each value of Brinell hardnesses at temperatures of 300°C and 400°C to a value of its Brinell hardness at a room-temperature.
  • each of the samples for comparison Nos. 1 to 3 which have a low silicon content outside the scope of the present invention, has a Brinell hardness at a temperature of 300°C within a range of from 83 to 85% of its room-temperature Brinell hardness, and a Brinell hardness at a temperature of 400°C within a range of from 65 to 68% of its room-temperature Brinell hardness, both of which are lower than the target values in the present invention.
  • the sample for comparison No. 4 which has a low carbon content outside the scope of the present invention has a room-temperature Brinell hardness of 150, which is far lower than the target value in the present invention.
  • Each of the samples of the invention Nos. 1 to 13 has, in contrast, a Brinell hardness at a room-temperature within a range of from 304 to 522, which is higher than the target value in the present invention, and has a Brinell hardness at a temperature of 300°C of at least 90% of its room-temperature Brinell hardness, which is the target value in the present invention, and has a Brinell hardness at a temperature 400°C of at least 70% of its room-temperature Brinell hardness, which is the target value in the present invention.
  • each of the samples of the invention Nos. 1 to 13 has an excellent wear resistance in the intermediate temperature region without largely increasing its room-temperature hardness.
  • a wear-resistant steel for the intermediate and room temperature service which has a Brinell hardness at a room-temperature of at least 250, and has a Brinell hardness at a temperature of 300°C of at least 90% of its room-temperature Brinell hardness, and a Brinell hardness at a temperature of 400°C of at least 70% of its room-temperature Brinell hardness, the last two Brinell hardnesses being available without largely increasing its room-temperature Brinell hardness, thus providing industrially useful effects.

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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 Steel (AREA)
EP91101082A 1990-02-20 1991-01-28 Acier résistant à l'usure pour utilisation à des températures intermédiaires et à la température ambiante Withdrawn EP0445519A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP37431/90 1990-02-20
JP3743190A JPH03243743A (ja) 1990-02-20 1990-02-20 中常温域で高い硬度を有する中常温用耐摩耗鋼

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Publication Number Publication Date
EP0445519A1 true EP0445519A1 (fr) 1991-09-11

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EP91101082A Withdrawn EP0445519A1 (fr) 1990-02-20 1991-01-28 Acier résistant à l'usure pour utilisation à des températures intermédiaires et à la température ambiante

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Country Link
EP (1) EP0445519A1 (fr)
JP (1) JPH03243743A (fr)
AU (1) AU7107891A (fr)
CA (1) CA2034874A1 (fr)
FI (1) FI910727A (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU669776B2 (en) * 1993-10-13 1996-06-20 Douglas G Bruce Method of producing primarily tempered martensite steel

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5131965A (en) * 1990-12-24 1992-07-21 Caterpillar Inc. Deep hardening steel article having improved fracture toughness
CN1293222C (zh) * 2003-12-11 2007-01-03 杨军 一种高硬度高韧性易火焰切割的耐磨钢板及其制备方法
US8684235B2 (en) 2007-02-14 2014-04-01 Kao Corporation Trigger-type liquid sprayer
TWI341332B (en) 2008-01-07 2011-05-01 Nippon Steel Corp Wear-resistant steel sheet having excellent wear resistnace at high temperatures and excellent bending workability and method for manufacturing the same
JP6459875B2 (ja) * 2015-09-25 2019-01-30 Ｊｆｅスチール株式会社 耐磨耗鋼板およびその製造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH317544A (de) * 1956-06-07 1956-11-30 Monteforno Acciajerie E Lamina Baustahl
US2863763A (en) * 1957-03-19 1958-12-09 Samuel J Rosenberg Ductile and tough high strength steel
SU266215A1 (fr) * 1968-01-09 1970-03-17 Чел бинский ордена Ленина завод дорожных машин Колющенко
GB1202513A (en) * 1969-01-15 1970-08-19 Stoody Co Process of forming a layer of added steel to a steel workpiece
SU342941A1 (fr) * 1970-01-20 1972-06-22 М. П. Браун, И. Н. Попов , Э. И. Мировский

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5442812A (en) * 1977-09-12 1979-04-05 Nat Jutaku Kenzai Method of constructing building
JPS5565350A (en) * 1978-11-10 1980-05-16 Mitsubishi Heavy Ind Ltd High toughness, wear resistant steel

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH317544A (de) * 1956-06-07 1956-11-30 Monteforno Acciajerie E Lamina Baustahl
US2863763A (en) * 1957-03-19 1958-12-09 Samuel J Rosenberg Ductile and tough high strength steel
SU266215A1 (fr) * 1968-01-09 1970-03-17 Чел бинский ордена Ленина завод дорожных машин Колющенко
GB1202513A (en) * 1969-01-15 1970-08-19 Stoody Co Process of forming a layer of added steel to a steel workpiece
SU342941A1 (fr) * 1970-01-20 1972-06-22 М. П. Браун, И. Н. Попов , Э. И. Мировский

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU669776B2 (en) * 1993-10-13 1996-06-20 Douglas G Bruce Method of producing primarily tempered martensite steel

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Publication number Publication date
CA2034874A1 (fr) 1991-08-21
AU7107891A (en) 1991-08-22
JPH03243743A (ja) 1991-10-30
FI910727A0 (fi) 1991-02-14
FI910727A (fi) 1991-08-21

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